High-density acicular hematite particles, non-magnetic undercoat layer and magnetic recording medium

ABSTRACT

High-density acicular hematite particles comprise acicular hematite particles and a coat comprising an oxide of tin or oxides of tin and antimony, formed on at least a part of surfaces of said acicular hematite particles; and have an average major axial diameter of not more than 0.3 μm, a pH value of not less than 8, a soluble sodium salt content of not more than 300 ppm, calculated as Na, and a soluble sulfate content of not more than 150 ppm, calculated as SO 4 . Such high-density acicular hematite particles is suitable as non-magnetic particles for a non-magnetic undercoat layer of a magnetic recording medium using magnetic particles containing iron as a main ingredient, have an excellent dispersibility in vehicle and a low volume resistivity.

This is a division of application Ser. No. 09/048,179, filed Mar. 26, 1998, now U.S. Pat. No. 6,207,279, the entire content of which is hereby incorporated by reference in this application.

BACKGROUND OF THE INVENTION

The present invention relates to high-density acicular hematite particles, a non-magnetic undercoat layer containing the high-density acicular hematite particles and a magnetic recording medium having the non-magnetic undercoat layer. More particularly, the present invention relates to high-density acicular hematite particles suitable as non-magnetic particles for a non-magnetic undercoat layer of a magnetic recording medium using magnetic particles containing iron as a main ingredient, which have an excellent dispersibility in binder resin, a pH value of not less than 8, a less content of soluble sodium salts and soluble sulfates, and a high surface conductivity; a non-magnetic undercoat layer containing the high-density acicular hematite particles and suitably used for a magnetic recording medium using magnetic particles containing iron as a main ingredient; and a magnetic recording medium having the non-magnetic undercoat layer.

With a development of miniaturized and lightweight video or audio magnetic recording and reproducing apparatuses for long-time recording, magnetic recording media such as a magnetic tape and magnetic disk have been increasingly and strongly required to have a higher performance, namely, a higher recording density, higher output characteristic, in particular, an improved frequency characteristic and a lower noise level.

Various attempts have been made at both enhancing the properties of magnetic particles and reducing the thickness of a magnetic recording layer in order to improve these properties of a magnetic recording medium.

The enhancement of the properties of magnetic particles will first be described.

Magnetic particles are required to have, in order to satisfy the above-described demands on a magnetic recording medium, properties such as a high coercive force and a large saturation magnetization.

As magnetic particles suitable for high-output and high-density recording, acicular magnetic particles containing iron as a main ingredient which are obtained by heat-treating acicular goethite particles or acicular hematite particles in a reducing gas are widely known.

Acicular magnetic particles containing iron as a main ingredient have a high coercive force and a large saturation magnetization, since the acicular magnetic particles containing iron as a main ingredient used for a magnetic recording medium are very fine particles having a particle size of not more than 1 μm, particularly, 0.01 to 0.3 μm. Therefore, such particles easily corrode, and the magnetic properties thereof are deteriorated, especially, the saturation magnetization and the coercive force are reduced.

In order to maintain the characteristics of a magnetic recording medium which uses magnetic particles containing iron as a main ingredient as the magnetic particles, over a long period, it is strongly demanded to suppress the corrosion of the acicular magnetic particles containing iron as a main ingredient as much as possible.

A reduction in the thickness of a magnetic recording layer will now be described.

Video tapes have recently been required more and more to have a higher picture quality, and the frequencies of carrier signals recorded in recent video tapes are higher than those recorded in conventional video tapes. In other words, the signals in the short-wave region have come to be used, and as a result, the magnetization depth from the surface of a magnetic tape has come to be remarkably small.

With respect to short wavelength signals, a reduction in the thickness of a magnetic recording layer is also strongly demanded in order to improve the high output characteristics, especially, an S/N ratio of a magnetic recording medium. This fact is described, for example, on page 312 of Development of Magnetic Materials and Technique for High Dispersion of Magnetic Powder, published by Sogo Gijutsu Center Co., Ltd. (1982), “. . . the conditions for high-density recording in a coated-layer type tape are that the noise level is low with respect to signals having a short wavelength and that the high output characteristics are maintained. To satisfy these conditions, it is necessary that the tape has large coercive force Hc and residual magnetization Br, and the coating film has a smaller thickness. . . . ”.

Development of a reduction in the thickness of a magnetic recording layer has caused some problems.

Firstly, it is necessary to make a magnetic recording layer smooth and to eliminate the non-uniformity of thickness. As well known, in order to obtain a smooth magnetic recording layer having a uniform thickness, the surface of the substrate must also be smooth. This fact is described on pages 180 and 181 of Materials for Synthetic Technology—Causes of Friction and Abrasion of Magnetic Tape and Head Running System and Measures for Solving the Problem (hereinunder referred to as “Materials for Synthetic Technology” (1987), published by the Publishing Department of Technology Information Center, “ . . . the surface roughness of a hardened magnetic layer depends on the surface roughness of the substrate (back surface roughness) so largely as to be approximately proportional, . . . , since the magnetic layer is formed on the substrate, the more smooth the surface of the substrate is, the more uniform and larger head output is obtained, and the more the S/N ratio is improved.”

Secondly, there has been caused a problem in the strength of a non-magnetic substrate such as a base film with a tendency of the reduction in the thickness of the non-magnetic substrate in response to the demand for a thinner magnetic layer. This fact is described, for example, on page 77 of the above-described Development of Magnetic Materials and Technique for High Dispersion of Magnetic Powder, “ . . . Higher recording density is a large problem assigned to the present magnetic tape. This is important in order to shorten the length of the tape and to miniaturize the size of a cassette and to enable long-time recording. For this purpose, it is necessary to reduce the thickness of a substrate . . . . With the tendency of reduction in the film thickness, the stiffness of the tape also reduces to such an extent as to make smooth travel in a recorder difficult. Therefore, improvement of the stiffness of a video tape both in the machine direction and in the transverse direction is now strongly demanded. . . . ”

The end portion of a magnetic recording medium such as a magnetic tape, especially, a video tape is judged by detecting a portion of the magnetic recording medium at which the light transmittance is large by a video deck. If the light transmittance of the whole part of a magnetic recording layer is made large by the thinner magnetic recording medium or the ultrafine magnetic particles dispersed in the magnetic recording layer, it is difficult to detect the portion having a large light transmittance by a video deck. For reducing the light transmittance of the whole part of a magnetic recording layer, carbon black or the like is added to the magnetic recording layer. It is, therefore, essential to add carbon black or the like to a magnetic recording layer in the present video tapes.

However, addition of a large amount of non-magnetic particles such as carbon black impairs not only the enhancement of the recording density but also the development of a thinner recording layer. Therefore in order to reduce the magnetization depth from the surface of the magnetic tape and to produce a thinner magnetic recording layer, it is strongly demanded to reduce, as much as possible, the quantity of non-magnetic particles such as carbon black which are added to a magnetic recording layer.

It is also strongly demanded that the light transmittance of a magnetic recording layer should be small even if the carbon black or the like which is added to the magnetic recording layer is reduced to a small amount. From this point of view, improvements in a substrate are now in strong demand.

Further, in order to reduce not only the above-mentioned optical transmittance but also surface resistivity of the magnetic recording medium, carbon black has been conventionally added to a magnetic recording layer thereof.

The use of carbon black in the magnetic recording medium is described in more detail below.

In the case where the magnetic recording medium has a high surface resistivity, the electrostatically charged amount on the magnetic recording medium is increased, so that cutting wastes of magnetic recording media or dusts are attached to the surface of magnetic recording medium upon production or use of the magnetic recording medium, thereby increasing occurrence of drop-out.

Consequently, in order to lower the surface resistivity of the magnetic recording medium to about 10⁸ Ωcm, a conductive compound such as carbon black has been generally added to a magnetic recording layer thereof in an amount of not less than about 5 parts by weight based on 100 parts by weight of magnetic particles used therein.

However, such an increase in amount of non-magnetic substance such as carbon black in the magnetic recording layer tends to cause the deterioration in signal recording property and inhibit the reduction in thickness of the magnetic recording layer.

Various efforts have been made to improve a base film for a magnetic recording layer with a demand for a thinner magnetic recording layer and a thinner non-magnetic substrate. A magnetic recording medium having at least one undercoat layer (hereinunder referred to “non-magnetic undercoat layer”) comprising a binder resin and non-magnetic particles containing iron as a main ingredient such as hematite particles which are dispersed therein, on a non-magnetic substrate such as a base film has been proposed and put to practical use (Japanese Patent Publication (KOKOKU) No. 6-93297 (1994), Japanese Patent Application Laid-Open (KOKAI) Nos. 62-159338 (1987), 63-187418 (1988), 4-167225 (1992), 4-325915 (1992), 5-73882 (1993), 5-182177 (1993), 5-347017 (1993), 6-60362 (1994), 9-35245 (1997), etc.)

Further, various attempts for reducing the content of carbon black in the magnetic recording layer and lowering the surface resistivity of the magnetic recording medium as low as possible, have been conducted. For example, it is known that the surfaces of non-magnetic particles dispersed in the above-mentioned non-magnetic undercoat layer are coated with a tin compound or an antimony compound (Japanese Patent Nos. 2566088 and 2566089, Japanese Patent Publication (KOKOKU) No. 5-33446(1993), Japanese Patent Applications Laid-open (KOKAI) Nos. 6-60360(1994), 7-176030(1995), 8-50718(1996), 8-203063(1996), 8-255334, 9-27116(1997) or the like).

For example, Japanese Patent Application Laid-Open (KOKAI) No. 5-182177 (1993) discloses a magnetic recording medium comprising: a non-magnetic substrate; a non-magnetic undercoat layer formed on the non-magnetic substrate and produced by dispersing inorganic particles in a binder resin; and a magnetic layer formed on the non-magnetic undercoat layer and produced by dispersing ferromagnetic particles in a binder resin while the non-magnetic undercoat layer is wet; wherein the magnetic layer has a thickness of not more than 1.0 μm in a dried state, the non-magnetic undercoat layer contains non-magnetic inorganic particles with surface layers coated with an inorganic oxide, the inorganic oxide coating the surfaces of the non-magnetic inorganic particles contained in the non-magnetic undercoat layer is at least one selected from the group consisting of Al₂O₃, SiO₂ and ZrO₂, and the amount of the inorganic oxide coating the non-magnetic inorganic particles is 1 to 21 wt % in the case of Al₂O₃, 0.04 to 20 wt % in the case of SiO₂, and 0.05 to 15 wt % in the case of ZrO₂, base on the total weigh of the magnetic inorganic particles.

In Japanese Patent No. 2566088, there is described a magnetic recording medium comprising a non-magnetic substrate, a non-magnetic undercoat layer formed on the non-magnetic substrate, comprising a binder resin and non-magnetic inorganic particles dispersed in the binder resin and coated with at least one oxide selected from the group consisting of Al₂O₃, SiO₂, ZrO₂, Sb₂O₃ and ZnO, and a magnetic uppercoat layer formed on the non-magnetic undercoat layer, comprising a binder resin and ferromagnetic particles dispersed in the binder resin, wherein the magnetic uppercoat layer has a dry thickness of not more than 1.0 μm; the non-magnetic undercoat layer has a dry thickness of 0.5 to 10 μm; and the ferromagnetic particles have a major axial diameter of not more than 0.3 μm.

At present, there has been more demanded non-magnetic particles for non-magnetic undercoat layer of a magnetic recording medium, which are capable of furnishing a non-magnetic undercoat layer having excellent surface smoothness and mechanical strength by dispersing the non-magnetic particles in a binder resin; which are capable of furnishing a magnetic recording layer having a surface smoothness and a thin and uniform thickness when the magnetic recording layer is formed on the non-magnetic undercoat layer; which are capable of furnishing a magnetic recording medium having a low transmittance and a low surface resistivity; and which are capable of preventing the corrosion of magnetic particles containing iron as a main ingredient, which are dispersed in the magnetic recording layer. However, such non-magnetic particles have not been furnished yet.

That is, it has been reported that the above-mentioned conventional magnetic recording medium using hematite particles as non-magnetic particles for non-magnetic undercoat layer thereof, are improved in surface smoothness and mechanical strength of the non-magnetic undercoat layer; is capable of forming a magnetic recording layer having a surface smoothness, and a thin and uniform thickness upon the formation of the magnetic recording layer; and exhibit a low transmittance. However, these properties reported are still unsatisfactory. Especially, as described in Comparative Examples hereinafter, the surface resistivity of these conventional magnetic recording medium is as high as 10⁹ to 10¹¹ Ωcm.

On the other hand, in the case of the magnetic recording medium having the non-magnetic undercoat layer containing non-magnetic particles coated with a tin compound or an antimony compound and dispersed in a binder resin, the non-magnetic undercoat layer is deteriorated in surface smoothness and mechanical strength, though the surface resistivity thereof is low. Accordingly, the magnetic recording layer formed on such a non-magnetic undercoat layer necessarily has a rough surface and an uneven thickness, and exhibit an unsatisfactory transmittance.

Further, there has also been pointed out such a problem that the magnetic particles containing iron as a main ingredient, which are dispersed in the magnetic recording layer, undergo server corrosion after the production of the magnetic recording medium, thereby causing the considerable deterioration in magnetic properties thereof.

As a result of the present inventors' earnest studies for solving the above-mentioned problems, it has been found that by coating at least a part of surfaces of specific acicular hematite particles with an oxide of tin or an oxide of tin and antimony, and controlling the pH value to not less than 8 and contents of soluble sodium salts and soluble sulfates to a certain range, the obtained high-density acicular hematite particles exhibit a low surface resistivity and an excellent dispersibility in a vehicle. The present invention has been attained on the basis of this finding.

SUMMARY OF THE INVENTION

It is an object of the present invention to provide non-magnetic particles for non-magnetic undercoat layer of a magnetic recording medium, which are capable of furnishing a non-magnetic undercoat layer having excellent surface smoothness and mechanical strength by dispersing the non-magnetic particles in a binder resin; which are capable of furnishing a magnetic recording layer having a surface smoothness and a thin and uniform thickness upon the formation of the magnetic recording layer; which are capable of furnishing a magnetic recording medium having a low transmittance and a low surface resistivity; and which are capable of preventing the corrosion of metal magnetic particles containing iron as a main ingredient, which are dispersed in the magnetic recording layer.

It is another object of the present invention to provide a non-magnetic undercoat layer which has excellent surface smoothness and mechanical strength, which is capable of forming thereon a magnetic recording layer, which is capable of imparting an excellent surface smoothness, a low transmittance and a low surface resistivity to the magnetic recording layer when formed on the non-magnetic undercoat layer, and which is capable of preventing metal magnetic particles containing iron as a main ingredient, which are dispersed in the magnetic recording layer, from being corroded, thereby inhibiting the deterioration in magnetic properties thereof.

It is other object of the present invention to provide a magnetic recording medium which has an excellent surface smoothness, a low transmittance and a low surface resistivity, and in which the corrosion of metal magnetic particles containing iron as a main ingredient, which are dispersed in the magnetic recording layer, is prevented, thereby inhibiting the deterioration in magnetic properties thereof.

To accomplish the aim, in a first aspect of the present invention, there is provided high-density acicular hematite particles comprising acicular hematite particles and a coat comprising an oxide of tin or oxides of tin and antimony, formed on at least a part of surfaces of the acicular hematite particles; and having an average major axial diameter of not more than 0.3 μm, a pH value of not less than 8, a soluble sodium salt content of not more than 300 ppm (calculated as Na) and a soluble sulfate content of not more than 150 ppm (calculated as SO₄).

In a second aspect of the present invention, there is provided high-density acicular hematite particles comprising acicular hematite particles, a first coat comprising an oxide of tin or oxides of tin and antimony, formed on at least a part of surfaces of the acicular hematite particles, and a second coat comprising at least one compound selected from the group consisting of a hydroxide of aluminum, an oxide of aluminum, a hydroxide of silicon and an oxide of silicon, formed on at least a part of surfaces of said high-density acicular hematite particles; and

having an average major axial diameter of not more than 0.3 μm, a pH value of not less than 8, a soluble sodium salt content of not more than 300 ppm (calculated as Na) and a soluble sulfate content of not more than 150 ppm (calculated as SO₄).

In a third aspect of the present invention, there is provided a non-magnetic undercoat layer comprising the high-density acicular hematite particles set forth in the first or second aspect and a binder resin, formed on a non-magnetic substrate.

In a fourth aspect of the present invention, there is provided a magnetic recording medium comprising:

a non-magnetic substrate;

a non-magnetic undercoat layer comprising the high-density acicular hematite particles set forth in the first or second aspect and a binder resin, formed on said non-magnetic substrate; and

a magnetic recording layer comprising magnetic particles containing iron as a main ingredient and a binder resin, formed on said non-magnetic undercoat layer.

In a fifth aspect of the present invention, there is provided a process for producing high-density acicular hematite particles set forth in claim 1, comprising:

heat-dehydrating acicular goethite particles coated with a hydroxide of tin to obtain low-density acicular hematite particles;

heat-treating said low-density acicular hematite particles at a temperature of not less than 550° C. to obtain high-density acicular hematite particles coated with an oxide of tin;

wet-pulverizing a slurry containing said high-density acicular hematite particles;

adjusting the pH value of said slurry to not less than 13;

heat-treating said slurry at a temperature of not less than 80° C.; and

filtering said slurry to separate high-density acicular hematite particles therefrom, followed by washing with water and drying.

In a sixth aspect of the present invention, there is provided a process for producing high-density acicular hematite particles set forth in claim 1, comprising:

wet-pulverizing a slurry containing high-density acicular hematite particles obtained by heat-treating at a temperature of not less than 550° C. low-density acicular hematite particles produced by heat-dehydrating acicular goethite particles coated with a sintering preventive agent;

adjusting the pH value of said slurry to not less than 13;

heat-treating said slurry at a temperature of not less than 80° C.; and

filtering said slurry to separate high-density acicular hematite particles therefrom, followed by washing with water and drying;

treating the obtained high-density acicular hematite particles with an aqueous solution containing a tin compound to obtain high-density acicular hematite particles coated with a hydroxide of tin; and

heat-treating said high-density acicular hematite particles coated with a hydroxide of tin at a temperature of not less than 300° C.

In a seventh aspect of the present invention, there is provided a process for producing high-density acicular hematite particles set forth in claim 1, comprising:

heat-dehydrating acicular goethite particles coated with hydroxides of tin and antimony to obtain low-density acicular hematite particles;

heat-treating said low-density acicular hematite particles at a temperature of not less than 550° C. to obtain high-density acicular hematite particles coated with oxides of tin and antimony;

wet-pulverizing a slurry containing said high-density acicular hematite particles;

adjusting the pH value of said slurry to not less than 13;

heat-treating said slurry at a temperature of not less than 80° C.; and

filtering said slurry to separate high-density acicular hematite particles therefrom, followed by washing with water and drying.

In an eighth aspect of the present invention, there is provided a process for producing high-density acicular hematite particles set forth in claim 1, comprising:

wet-pulverizing a slurry containing high-density acicular hematite particles obtained by heat-treating at a temperature of not less than 550° C. low-density acicular hematite particles produced by heat-dehydrating acicular goethite particles coated with a sintering preventive agent;

adjusting the pH value of said slurry to not less than 13;

heat-treating said slurry at a temperature of not less than 80° C.; and

filtering said slurry to separate high-density acicular hematite particles therefrom, followed by washing with water and drying;

treating the obtained high-density acicular hematite particles with an aqueous solution containing a tin compound and an antimony compound to obtain high-density acicular hematite particles coated with hydroxides of tin and antimony; and

heat-treating said high-density acicular hematite particles coated with hydroxides of tin and antimony at a temperature of not less than 300° C.

DETAILED DESCRIPTION OF THE INVENTION

The present invention is described in detail below.

First, the high-density acicular hematite particles in which at least a part of the surface thereof is coated with an oxide of tin or an oxide of tin and antimony, are described.

The amount of the oxide of tin coated on surface of the particles is usually 0.5 to 500% by weight (calculated as Sn) based on the weight of the acicular hematite particles. When the amount of the oxide of tin is less than 0.5% by weight, the surface of the particles cannot be satisfactorily coated with the oxide of tin as a conductive substance, so that it becomes impossible to attain a sufficient effect of reducing a surface resistivity of the magnetic recording medium. On the other hand, when the amount of the oxide of tin is more than 500% by weight, although a sufficient effect of reducing a surface resistivity of the magnetic recording medium can be obtained, the effect is already saturated and, therefore, the use of such an excessive amount of the oxide of tin is meaningless. In view of the surface resistivity of the obtained magnetic recording medium and economy of the production thereof, the amount of the oxide of tin is preferably 1.0 to 250% by weight, more preferably 2.0 to 200% by weight (calculated as Sn) based on the weight of the acicular hematite particles.

The amount of the oxide of antimony coated on surfaces of the particles is usually not more than 50% by weight, preferably 0.05 to 50% by weight (calculated as Sb) based on the weight of the acicular hematite particles. When the amount of the oxide of antimony is more than 50% by weight, although a sufficient effect of reducing a surface resistivity of the magnetic recording medium can be obtained, the effect is already saturated and, therefore, the use of such an excessive amount of the oxide of antimony is meaningless. In view of the surface resistivity of the obtained magnetic recording medium and economy of the production thereof, the amount of the oxide of antimony is more preferably 0.1 to 25% by weight (calculated as Sb) based on the weight of the acicular hematite particles.

In the case where the surface of the particles are coated with the oxide of tin and antimony, the weight ratio of tin to antimony is usually 20:1 to 1:1, preferably 15:1 to 2:1. When the amount of tin is less than that of antimony, it may become difficult to effectively reduce a surface resistivity of the magnetic recording medium. When the weight ratio of tin to antimony exceeds 20, it may become difficult to more effectively reduce a surface resistivity of the magnetic recording medium, because the amount of tin is too small.

The high-density acicular hematite particles coated with the oxide of tin or the oxides of tin and antimony according to the present invention have an average major axial diameter of not more than 0.3 μm, a pH value of not less than 8, a soluble sodium salt content of not more than 300 ppm (calculated as Na) and a soluble sulfate content of not more than 150 ppm (calculated as SO₄).

The high-density acicular hematite particles in the present invention have an aspect ratio (average major axial diameter/average minor axial diameter) (hereinunder referred to merely as “aspect ratio”) of not less than 2:1, preferably not less than 3:1. The upper limit of the aspect ratio is usually 20:1, preferably 10:1 with the consideration of the dispersibility in the vehicle. The shape of the acicular particles here may have not only acicular but also spindle-shaped, rice ball-shaped or the like.

When the aspect ratio is less than 2:1, it is difficult to obtain a desired film strength of the magnetic recording medium.

The average major axial diameter of the high-density acicular hematite particles of the present invention is not more than 0.3 μm, preferably 0.005 to 0.3 μm. When the average major axial diameter exceeds 0.3 μm, the particle size is so large as to impair the surface smoothness. With the consideration of the dispersibility in the vehicle and the surface smoothness of the coated film, the more preferable average major axial diameter is 0.02 to 0.2 μm.

The average minor axial diameter of the high-density acicular hematite particles of the present invention is usually 0.0025 to 0.15 μm. When the average minor axial diameter is less than 0.0025 μm, dispersion in the vehicle may be unfavorably difficult. On the other hand, when the average minor axial diameter exceeds 0.15 μm, the particle size may be apt to become so large as to impair the surface smoothness. With the consideration of the dispersibility in the vehicle and the surface smoothness of the coated film, the more preferable average minor axial diameter is 0.01 to 0.10 μm.

The BET specific surface area of the high-density acicular hematite particle of the present invention is usually not less than 35 m²/g. When it is less than 35 m²/g, the acicular hematite particles may be coarse or sintering may be sometimes caused between particles, which are apt to exert a deleterious influence on the surface smoothness of the coated film. The BET surface area thereof is more preferably not less than 40 m²/g, even more preferably not less than 45 m²/g, and the upper limit thereof is usually 150 m²/g. The upper limit is preferably 100 m²/g, more preferably 80 m²/g with the consideration of the dispersibility in the vehicle.

The degree of densification (S_(BET)/S_(TEM)) of hematite particles is represented by the ratio of the specific surface area (S_(BET)) measured by a BET method and the surface area (S_(TEM)) calculated from the major axial diameter and the minor axial diameter which were measured from the particles in an electron micrograph.

The S_(BET)/S_(TEM) value of hematite particles according to the present invention is usually 0.5 to 2.5. When the S_(BET)/S_(TEM) value is less than 0.5, although the hematite particles have been densified, the particles may adhere to each other due to sintering therebetween, and the particle size may increase, so that a sufficient surface smoothness of the coated film may be not obtained. On the other hand, when the S_(BET)/S_(TEM) value exceeds 2.5, there may be many pores in the surfaces of particles and the dispersibility in the vehicle may become insufficient. In consideration of the surface smoothness of the coated film and the dispersibility in the vehicle, the S_(BET)/S_(TEM) value is preferably 0.7 to 2.0, more preferably 0.8 to 1.6.

The major axial diameter distribution of the high-density acicular hematite particles of the present invention is preferably not more than 1.50 in geometrical standard deviation. When it exceeds 1.50, the coarse particles existent sometimes exert a deleterious influence on the surface smoothness of the coated film. The major axial diameter distribution is more preferably not more than 1.40, even more preferably not more than 1.35 in geometrical standard deviation with the consideration of the surface smoothness of the coated film. From the point of view of industrial productivity, the major axial diameter distribution of the high-density acicular hematite particles obtained is usually 1.01 in geometrical standard deviation.

The pH value of the high-density acicular hematite particles of the present invention is not less than 8. When it is less than 8, the magnetic particles containing iron as a main ingredient contained in the magnetic recording layer formed on the non-magnetic undercoat layer are gradually corroded, thereby causing a deterioration in the magnetic properties. With the consideration of a corrosion preventive effect on the magnetic particles containing iron as a main ingredient, the pH value of the particles is preferably not less than 8.5, more preferably not less than 9.0. The upper limit is usually 12, preferably 11, more preferably 10.5.

The content of soluble sodium salts in the high-density acicular hematite particles of the present invention is not more than 300 ppm soluble sodium (calculated as Na). When it exceeds 300 ppm, the magnetic particles containing iron as a main ingredient contained in the magnetic recording layer formed on the non-magnetic undercoat layer are gradually corroded, thereby causing a deterioration in the magnetic properties. In addition, the dispersion property of the high-density acicular hematite particles in the vehicle is easily impaired, and the preservation of the magnetic recording medium is deteriorated and efflorescence is sometimes caused in a highly humid environment. With the consideration of a corrosion preventive effect on the magnetic particles containing iron as a main ingredient, the content of soluble sodium salt is preferably not more than 250 ppm, more preferably not more than 200 ppm, even more preferably not more than 150 ppm. From the point of view of industry such as productivity, the lower limit thereof is preferably about 0.01 ppm.

The content of soluble sulfate in the high-density acicular hematite particles of the present invention is not more than 150 ppm soluble sulfate (calculated as SO₄). When it exceeds 150 ppm, the magnetic particles containing iron as a main ingredient contained in the magnetic recording layer formed on the non-magnetic undercoat layer are gradually corroded, thereby causing a deterioration in the magnetic properties. In addition, the dispersion property of the high-density acicular hematite particles in the vehicle is easily impaired, and the preservation of the magnetic recording medium is deteriorated and efflorescence is sometimes caused in a highly humid environment. With the consideration of a corrosion preventive effect on the magnetic particles containing iron as a main ingredient, the content of soluble sulfate is preferably not more than 70 ppm, more preferably not more than 50 ppm. From the point of view of industry such as productivity, the lower limit thereof is preferably about 0.01 ppm.

The high-density acicular hematite particles according to the present invention in which at least a part of the surface thereof is coated with the oxide of tin or the oxide of tin and antimony, have a volume resistivity of 10³ to 5×10⁷ Ωcm. When the volume resistivity of acicular hematite particles is more than 10⁸ Ωcm, it may become difficult to obtain a magnetic recording medium having a sufficiently low surface resistivity.

At least a part of the surfaces of the high-density acicular hematite particles coated of the present invention may be coated with at least one selected from the group consisting of a hydroxide of aluminum, an oxide of aluminum, a hydroxide of silicon and an oxide of silicon. When the acicular hematite particles coated with the above-described coating material are dispersed in a vehicle, they have an affinity with the binder resin and it is easy to obtain a desired dispersibility.

The amount of aluminum hydroxide, aluminum oxide, silicon hydroxide or silicon oxide used as the coating material is usually not less than 50 wt %, preferably 0.01 to 50 wt % (calculated as Al or SiO₂). When it is less than 0.01 wt %, the dispersibility improving effect may be insufficient. When the amount exceeds 50 wt %, the coating effect becomes saturated, so that it is meaningless to add a coating material more than necessary. From the point of view of dispersibility in the vehicle, the preferable amount of coating material is preferably 0.05 to 20 wt % (calculated as Al or SiO₂).

Various properties of the high-density acicular hematite particles coated with a coating material of the present invention, such as aspect ratio, average major axial diameter, average minor axial diameter, pH value, the content of soluble sodium salt, content of soluble sulfate, BET specific surface area, major axial diameter distribution, degree of densification, and volume resistivity are approximately equivalent in values to those of the high-density acicular hematite particles of the present invention the surfaces of which are not coated with a coating material.

A non-magnetic undercoat layer and a magnetic recording medium according to the present invention will now be explained.

The magnetic medium of according to the present invention comprises a non-magnetic substrate, a non-magnetic undercoat layer and a magnetic recording layer.

The non-magnetic undercoat layer of the present invention is produced by forming a coating film on the non-magnetic substrate and drying the coating film. The non-magnetic coating film is formed by applying to the surface of the non-magnetic substrate a non-magnetic coating composition which contains the high-density acicular hematite particles, a binder resin and a solvent.

As the non-magnetic substrate, the following materials which are at present generally used for the production of a magnetic recording medium are usable as a raw material: a synthetic resin such as polyethylene terephthalate, polyethylene, polypropylene, polycarbonate, polyethylene naphthalate, polyamide, polyamideimide and polyimide; foil and plate of a metal such as aluminum and stainless steel; and various kinds of paper. The thickness of the non-magnetic substrate varies depending upon the material, but it is usually about 1.0 to 300 μm, preferably 2.0 to 200 μm. In the case of a magnetic disc, polyethylene terephthalate is ordinarily used as the non-magnetic substrate. The thickness thereof is usually 50 to 300 μm, preferably 60 to 200 μm. In the case of a magnetic tape, when polyethylene terephthalate is used as the non-magnetic substrate, the thickness thereof is usually 3 to 100 μm, preferably 4 to 20 μm. When polyethylene naphthalate is used, the thickness thereof is usually 3 to 50 μm, preferably 4 to 20 μm. When polyamide is used, the thickness thereof is usually 2 to 10 μm, preferably 3 to 7 μm.

The thickness of the non-magnetic undercoat layer obtained by coating the non-magnetic substrate with a coating composition and drying the coating film, is usually 0.2 to 10.0 μm, preferably 0.5 to 5.0 μm. When the thickness is less than 0.2 μm, not only it is impossible to ameliorate the surface roughness of the non-magnetic substrate but also the strength is insufficient.

As the binder resin in the present invention, the following resins which are at present generally used for the production of a magnetic recording medium are usable: vinyl chloride-vinyl acetate copolymer, urethane resin, vinyl chloride-vinyl acetate-maleic acid copolymer, urethane elastomer, butadiene-acrylonitrile copolymer, polyvinyl butyral, cellulose derivative such as nitrocellulose, polyester resin, synthetic rubber resin such as polybutadiene, epoxy resin, polyamide resin, polyisocyanate, electron radiation curing acryl urethane resin and mixtures thereof. Each of these resin binders may contain a functional group such as —OH, —COOH, —SO₃M, —OPO₂M₂ and —NH₂, wherein M represents H, Na or K. With the consideration of the dispersibility of the particles, a binder resin containing a functional group —COOH or —SO₃M is preferable.

The mixing ratio of the high-density acicular hematite particles with the binder resin is usually 5 to 2000 parts by weight, preferably 100 to 1000 parts by weight based on 100 parts by weight of the binder resin.

It is possible to add a lubricant, a polishing agent, an antistatic agent, etc. which are generally used for the production of a magnetic recording medium to the non-magnetic undercoat layer.

The gloss of the coated film of the non-magnetic undercoat layer containing high-density acicular hematite particles according to the present invention is usually 180 to 280%, preferably 185 to 280%, more preferably 187 to 280% and the surface roughness Ra thereof is usually 2.0 to 13.0 nm, preferably 2.0 to 11.0 nm, more preferably 2.0 to 10.0 nm. The Young's modulus (relative value to a commercially available video tape: AV T-120 produced by Victor Company of Japan, Limited) thereof is usually 115 to 150, preferably 120 to 150, more preferably 125 to 150.

The magnetic recording medium according to the present invention is produced by forming the non-magnetic undercoat layer formed on the non-magnetic substrate, forming a coating film on the non-magnetic undercoat layer by applying a coating composition containing magnetic particles containing iron as a main ingredient, a binder resin and a solvent, and drying the coating film to obtain a magnetic recording layer.

The magnetic particles containing iron as a main ingredient used in the present invention comprises iron or iron and at least one selected from the group consisting of Co, Al, Ni, P, Si, Zn, Ti, Cu, B, Nd, La and Y. Further, the following magnetic particles containing iron as a main ingredient may be exemplified.

1) Magnetic particles containing iron as a main ingredient comprises iron and usually 0.05 to 10 wt %, preferably 0.1 to 7 wt % of aluminum (calculated as Al) based on the weight of the magnetic particles containing iron as a main ingredient.

2) Magnetic particles containing iron as a main ingredient comprises iron; usually 0.05 to 10 wt %, preferably 0.1 to 7 wt % of aluminum (calculated as Al) based on the weight of the magnetic particles containing iron as a main ingredient; and usually 0.05 to 40 wt %, preferably 1.0 to 35 wt %, more preferably 3 to 30 wt % of cobalt (calculated as Co) based on the weight of the magnetic particles containing iron as a main ingredient.

3) Magnetic particles containing iron as a main ingredient comprises iron; usually 0.05 to 10 wt %, preferably 0.1 to 7 wt % of aluminum (calculated as Al) based on the weight of the magnetic particles containing iron as a main ingredient; and usually 0.05 to 10 wt %, preferably 0.1 to 7 wt % of at least one selected from the group consisting of Nd, La and Y (calculated as the corresponding element) based on the weight of the magnetic particles containing iron as a main ingredient.

4) Magnetic particles containing iron as a main ingredient comprises iron; usually 0.05 to 10 wt %, preferably 0.1 to 7 wt % of aluminum (calculated as Al) based on the weight of the magnetic particles containing iron as a main ingredient; usually 0.05 to 40 wt %, preferably 1.0 to 35 wt %, more preferably 3 to 30 wt % of cobalt (calculated as Co) based on the weight of the magnetic particles containing iron as a main ingredient; and usually 0.05 to 10 wt %, preferably 0.1 to 7 wt % of at least one selected from the group consisting of Nd, La and Y (calculated as the corresponding element) based on the weight of the magnetic particles containing iron as a main ingredient.

5) Magnetic particles containing iron as a main ingredient comprises iron; usually 0.05 to 10 wt %, preferably 0.1 to 7 wt % of aluminum (calculated as Al) based on the weight of the magnetic particles containing iron as a main ingredient; and usually 0.05 to 10 wt %, preferably 0.1 to 7 wt % of at least one selected from the group consisting of Ni, P, Si, Zn, Ti, Cu and B (calculated as the corresponding element) based on the weight of the magnetic particles containing iron as a main ingredient.

6) Magnetic particles containing iron as a main ingredient comprises iron; usually 0.05 to 10 wt %, preferably 0.1 to 7 wt % of aluminum (calculated as Al) based on the weight of the magnetic particles containing iron as a main ingredient; usually 0.05 to 40 wt %, preferably 1.0 to 35 wt %, more preferably 3 to 30 wt % of cobalt (calculated as Co) based on the weight of the magnetic particles containing iron as a main ingredient; and usually 0.05 to 10 wt %, preferably 0.1 to 7 wt % of at least one selected from the group consisting of Ni, P, Si, Zn, Ti, Cu and B (calculated as the corresponding element) based on the weight of the magnetic particles containing iron as a main ingredient.

7) Magnetic particles containing iron as a main ingredient comprises iron; usually 0.05 to 10 wt %, preferably 0.1 to 7 wt % of aluminum (calculated as Al) based on the weight of the magnetic particles containing iron as a main ingredient; usually 0.05 to 10 wt %, preferably 0.1 to 7 wt % of at least one selected from the group consisting of Nd, La and Y (calculated as the corresponding element) based on the weight of the magnetic particles containing iron as a main ingredient; and usually 0.05 to 10 wt %, preferably 0.1 to 7 wt % of at least one selected from the group consisting of Ni, P, Si, Zn, Ti, Cu and B (calculated as the corresponding element) based on the weight of the magnetic particles containing iron as a main ingredient.

8) Magnetic particles containing iron as a main ingredient comprises iron; usually 0.05 to 10 wt %, preferably 0.1 to 7 wt % of aluminum (calculated as Al) based on the weight of the magnetic particles containing iron as a main ingredient; usually 0.05 to 40 wt %, preferably 1.0 to 35 wt %, more preferably 3 to 30 wt % of cobalt (calculated as Co) based on the weight of the magnetic particles containing iron as a main ingredient; usually 0.05 to 10 wt %, preferably 0.1 to 7 wt % of at least one selected from the group consisting of Nd, La and Y (calculated as the corresponding element) based on the weight of the magnetic particles containing iron as a main ingredient; and usually 0.05 to 10 wt %, preferably 0.1 to 7 wt % of at least one selected from the group consisting of Ni, P, Si, Zn, Ti, Cu and B (calculated as the corresponding element) based on the weight of the magnetic particles containing iron as a main ingredient.

The iron content in the particles is the balance, and is preferably 50 to 99 wt %, more preferably 60 to 95 wt % (calculated as Fe) based on the weight of the magnetic particles containing iron as a main ingredient.

The magnetic particles containing iron as a main ingredient comprising (i) iron and Al; (ii) iron, Al and Co, (iii) iron, Al and at least one rare-earth metal such as Nd, La and Y, or (iv) iron, Al, Co and at least one rare-earth metal such as Nd, La and Y, are preferable from the point of the durability of the magnetic recording medium. Further, the magnetic particles containing iron as a main ingredient comprising iron, Al and at least one rare-earth metal such as Nd, La and Y, are more preferable.

The acicular magnetic particles containing iron as a main ingredient used in the present invention have an average major axial diameter of usually 0.01 to 0.50 μm, preferably 0.03 to 0.30 μm, more preferably 0.03 to 0.25 μm, an average minor axial diameter of usually 0.0007 to 0.17 μm, preferably 0.003 to 0.10 μm, and an aspect ratio of usually not less than 3:1, preferably and not less than 5:1. The upper limit of the aspect ratio is usually 15:1, preferably 10:1 with the consideration of the dispersibility in the vehicle. The shape of the acicular magnetic particles containing iron as a main ingredient may have not only acicular but also a spindle-shaped, rice ball-shaped or the like.

As to the magnetic properties of the acicular magnetic particles containing iron as a main ingredient used in the present invention, the coercive force is preferably 1200 to 3200 Oe, more preferably 1500 to 3200 Oe, and the saturation magnetization is preferably 100 to 170 emu/g, more preferably 130 to 170 emu/g with the consideration of the properties such as high-density recording.

As the binder resin for the magnetic recording layer, the same binder resin as that used for the production of the non-magnetic undercoat layer is usable.

The thickness of the magnetic recording layer obtained by applying the magnetic coating composition to the non-magnetic undercoat layer and dried, is ordinarily in the range of 0.01 to 5.0 μm. When the thickness is less than 0.01 μm, uniform coating may be difficult, so that unfavorable phenomenon such as unevenness on the coating surface is observed. On the other hand, when the thickness exceeds 5.0 μm, it may be difficult to obtain desired signal recording property due to an influence of diamagnetism. The preferable thickness is in the range of 0.05 to 1.0 μm.

The mixing ratio of the acicular magnetic particles containing iron as a main ingredient with the binder resin in the magnetic recording layer is usually 200 to 2000 parts by weight, preferably 300 to 1500 parts by weight based on 100 parts by weight of the binder resin.

It is possible to add a lubricant, a polishing agent, an antistatic agent, etc. which are generally used for the production of a magnetic recording medium to the magnetic recording layer.

The magnetic recording medium according to the present invention has a coercive force of usually 900 to 3500 Oe, preferably 1000 to 3500 Oe, more preferably 1500 to 3500 Oe; a squareness (residual magnetic flux density Br/saturation magnetic flux density Bm) of usually 0.85 to 0.95, preferably 0.87 to 0.95; a gloss (of the coating film) of usually 195 to 300%, preferably 200 to 300%; a surface roughness Ra (of the coating film) of usually not more than 11.0 nm, preferably 1.0 to 10.0 nm, more preferably 1.0 to 9.0 nm; a Young's modulus (relative value to a commercially available video tape: AV T-120 produced by Victor Company of Japan, Limited) of usually not less than 125, preferably not less than 130; a linear adsorption coefficient (of the coating film) of usually 1.10 to 2.00 μm⁻¹, preferably 1.20 to 2.00 μm⁻¹; and a surface resistivity (of the coating film) of usually 10⁴ to 5×10⁸ Ω/sq, preferably 10⁴ to 4.5×10⁸ Ω/sq, more preferably 10⁴ to 4×10⁸ Ω/sq.

The corrosiveness represented by a percentage (%) of change in the coercive force is usually not more than 10.0%, preferably not more than 9.5%, and the corrosiveness represented by a percentage (%) of change in the saturation magnetic flux density Bm is usually not more than 10.0%, preferably not more than 9.5%.

Next, the process for producing the high-density acicular hematite particles coated with an oxide of tin or both an oxide of tin and an oxide of antimony according to the present invention, is described below.

As a starting material for the acicular hematite particles, there may be used acicular goethite particles.

In order to produce the high-density acicular hematite particles of the present invention, acicular goethite particles are produced. Acicular goethite particles are produced by an ordinary method:

(A) a method of oxidizing a suspension having a pH value of not less than 11 and containing colloidal ferrous hydroxide particles which is obtained by adding not less than an equivalent of an alkali hydroxide solution to an aqueous ferrous salt solution, by passing an oxygen-containing gas thereinto at a temperature of not higher than 80° C.;

(B) a method of producing acicular goethite particles by oxidizing a suspension containing FeCO₃ which is obtained by reacting an aqueous ferrous salt solution with an aqueous alkali carbonate solution, by passing an oxygen-containing gas thereinto after aging, if necessary, the suspension;

(C) a method of growing acicular seed goethite particles by oxidizing a ferrous hydroxide solution containing colloidal ferrous hydroxide particles which is obtained by adding less than an equivalent of an alkali hydroxide solution or an alkali carbonate solution to an aqueous ferrous salt solution, by passing an oxygen-containing gas thereinto, thereby producing acicular seed goethite particles, adding not less than an equivalent of an alkali hydroxide solution to the Fe²⁺ in the aqueous ferrous salt solution, to the aqueous ferrous salt solution containing the acicular goethite seed particles, and passing an oxygen-containing gas into the aqueous ferrous salt solution; and

(D) a method of growing acicular seed goethite particles by oxidizing a ferrous hydroxide solution containing colloidal ferrous hydroxide particles which is obtained by adding less than an equivalent of an alkali hydroxide solution or an alkali carbonate solution to an aqueous ferrous salt solution, by passing an oxygen-containing gas thereinto, thereby producing acicular seed goethite particles, and growing the obtained acicular seed goethite particles in an acidic or neutral region.

Elements other than Fe such as Ni, Zn, P, Al and Si, which are generally added in order to enhance various properties of the particles such as the major axial diameter, the minor axial diameter and the aspect ratio, may be added during the reaction system for producing the goethite particles.

The acicular goethite particles obtained have an average major axial diameter of usually 0.005 to 0.4 μm, an average minor axial diameter of usually 0.0025 to 0.20 μm and a BET specific of about usually 50 to 250 m²/g, and contain ordinarily soluble sodium salts of 300 to 1500 ppm soluble sodium (calculated as Na) and ordinarily soluble sulfates of 100 to 3000 ppm soluble sulfate (calculated as SO₄).

The surfaces of the above-mentioned acicular goethite particles are then coated with a hydroxide of tin or hydroxides of tin and antimony.

In the coating-treatment, a tin compound or a tin compound and an antimony compound is added to a water suspension obtained by dispersing the acicular goethite particles in an aqueous solution. The suspension is stirred and if required, the pH value of the suspension is adjusted properly to coat the acicular goethite particles with the hydroxide of tin or the hydroxides of tin and antimony. Then, the suspension is then filtered to separate the coated acicular goethite particles therefrom. The coated acicular goethite particles is further washed with water, dried and pulverized.

As the tin compound added, there may be exemplified alkali stannates such as sodium stannate, tin salts such as stannous chloride, stannic chloride, stannous sulfate, stannic sulfate, stannous nitrate, stannic nitrate, stannous acetate or stannic acetate, or the like. The amount of the tin compound added is usually 0.5 to 500% by weight, preferably 1 to 250% by weight (calculated as Sn) based on the weight of the acicular goethite particles. When the amount of the tin compound added is less than 0.5% by weight, the acicular goethite particles cannot be sufficiently coated with the hydroxide of tin. On the other hand, when the amount of the tin compound added is more than 500% by weight, the effect by the addition is saturated and, therefore, the addition of such an excessive amount of the tin compound is meaningless.

As the antimony compound added, there may be exemplified antimony salts such as antimonous chloride, antimonic chloride or antimony sulfate. The amount of the antimony compound added is usually not more than 50% by weight, preferably 0.05 to 50% by weight (calculated as Sb) based on the weight of the acicular goethite particles. When the amount of the antimony compound added is more than 50% by weight, the effect by the addition is saturated and, therefore, the addition of such an excessive amount of the antimony compound is meaningless.

The thus obtained acicular goethite particles coated with the hydroxide of tin or the hydroxides of tin and antimony are heated at a temperature as high as not less than 550° C. to produce high-density acicular hematite particles. Alternatively, the coated acicular goethite particles may be heat-dehydrated at a temperature of 250 to 500° C. form low-density acicular hematite particles, and then, are heat-treated at a temperature as high as not less than 550° C. to produce high-density acicular hematite particles. In order to obtain the high-density acicular hematite particles maintaining the shape or configuration of original acicular goethite particles, the latter method is preferred.

It is preferred to coat the particles with a sintering preventive before the heat-treatment at a high temperature in order to obtain high-density acicular hematite particles which retain the shapes of the acicular goethite particles. The acicular goethite particles coated with a sintering preventive contain soluble sodium salts of usually 500 to 2000 ppm soluble sodium (calculated as Na) and soluble sulfates of usually 300 to 3000 ppm soluble sulfate (calculated as SO₄), and have the BET specific surface area of usually about 50 to 250 m²/g. The coating-treatment using a sintering preventive is composed of the steps of: adding a sintering preventive to an aqueous suspension containing the acicular goethite particles, mixing and stirring the suspension, filtering out the particles, washing the particles with water, and drying the particles.

Incidentally, in the case of the acicular goethite particles coated with the hydroxide of tin or the hydroxides of tin and antimony, the hydroxide of tin or the hydroxides of tin and antimony works on as sintering-preventive agent, and therefore, such coated acicular goethite particles may further be coated with the sintering-preventive agent.

The amount of sintering preventive existent on the surfaces of the acicular hematite particles of the present invention varies depending upon various conditions such as the kind of sintering preventive, the pH value thereof in an aqueous alkali solution and the heating temperature, it is usually not more than 10 wt %, preferably 0.05 to 10 wt % based on the total weight of the particles.

As the sintering preventive, sintering preventives generally used are usable. For example, phosphorus compounds such as sodium hexametaphosphate, polyphospholic acid and orthophosphoric acid; silicon compounds such as #3 water glass, sodium orthosilicate, sodium metasilicate and colloidal silica; boron compounds such as boric acid; aluminum compounds including aluminum salts such as aluminum acetate, aluminum sulfate, aluminum chloride and aluminum nitride, alkali aluminate such as sodium aluminate, and alumina sol and aluminum hydroxide; and titanium compounds such as titanyl sulfate may be exemplified.

The low-density acicular hematite particles obtained by heat-treating the acicular goethite particles coated with a sintering preventive at a temperature of 250 to 500° C. have an average major axial diameter of usually 0.005 to 0.30 μm, an average minor axial diameter of usually 0.0025 to 0.15 μm, a BET specific surface area of usually about 70 to 350 m²/g and contain soluble sodium salts of usually 500 to 2000 ppm soluble sodium (calculated as Na) and soluble sulfates of usually 300 to 4000 ppm soluble sulfate (calculated as SO₄). When the temperature for heat-treating the goethite particles is less than 250° C., the dehydration reaction takes a long time. On the other hand, When the temperature exceeds 500° C., the dehydration reaction is abruptly brought out, so that it is difficult to retain the shapes because the sintering between particles is caused. The low-density acicular hematite particles obtained by heat-treating the goethite particles at a low temperature are low-density particles having a large number of dehydration pores through which H₂O is removed from the goethite particles and the BET specific surface area thereof is about 1.2 to 2 times larger than that of the acicular goethite particles as the starting material.

The low-density hematite particles are then heat-treated at a temperature of not less than 550° C. to obtain a high-density acicular hematite particles. The upper limit of the heating temperature is preferably 850° C. The high-density hematite particles contain soluble sodium salts of usually 500 to 4000 ppm soluble sodium (calculated as Na) and soluble sulfates of usually 300 to 5000 ppm soluble sulfate (calculated as SO₄), and the BET specific surface area thereof is usually about 35 to 150 m²/g.

When the heat-treating temperature is less than 550° C., since the densification is insufficient, a large number of dehydration pores exist within and on the surface of the hematite particles, so that the dispersion in the vehicle is insufficient. Further, when the non-magnetic undercoat layer is formed from these particles, it is difficult to obtain a coated film having a smooth surface. On the other hand, when the temperature exceeds 850° C., although the densification of the hematite particles is sufficient, since sintering is caused on and between particles, the particle size increases, so that it is difficult to obtain a coated film having a smooth surface.

The obtained acicular hematite particles are pulverized by a dry-process, and formed into a slurry. The obtained slurry is then pulverized by a wet-process so as to deagglomerate coarse particles. In the wet-pulverization, ball mill, sand grinder, colloid mill or the like is used and wet-pulverization is conducted until coarse particles having a particle size of at least 44 μm are substantially removed. That is, the wet-pulverization is carried out until the amount of the coarse particles having a particle size of not less than 44 μm becomes to usually not more than 10% by weight, preferably not more than 5% by weight, more preferably 0% by weight based on the total weight of the particles. When the amount of the coarse particles having a particle size of not less than 44 μm is more than 10% by weight, the effect of treating the particles in an aqueous alkali solution at the next step is not attained.

The acicular hematite particles with coarse particles removed therefrom are heat-treated in a slurry at a temperature of usually not less than 80° C. after the pH value of the slurry is adjusted to not less than 13 by adding an aqueous alkali solution such as sodium hydroxide.

The concentration of the alkali suspension containing the acicular hematite particles and having a pH value of not less than 13 is preferably 50 to 250 g/liter.

When the pH value of the alkali suspension containing the acicular hematite particles is less than 13, it is impossible to effectively remove the solid crosslinking caused by the sintering preventive which exists on the surfaces of the hematite particles, so that it is impossible to wash out the soluble sodium slat, soluble sulfate, etc. existing within and on the surfaces of the particles. The upper limit of the pH value is usually about 14. When the effect of removing the solid crosslinking caused by the sintering preventive which exists on the surfaces of the hematite particles, the effect of washing out the soluble sodium slat, soluble sulfate, etc., and the effect of removing the alkali which adheres to the surfaces of hematite particles in the process of the heat-treatment of the aqueous alkali suspension are taken into consideration, the preferable pH value thereof is in the range of 13.1 to 13.8.

The heat-treating temperature in the aqueous alkali suspension which contains the acicular hematite particles and has a pH value of not less than 13, is usually not less than 80° C., preferably not less than 90° C. If the temperature is less than 80° C., it is difficult to effectively remove the solid crosslinking caused by the sintering preventive which exists on the surfaces of the hematite particles. The upper limit of the heating temperature is preferably 103° C., more preferably 100° C. When the heating temperature exceeds 103° C., although it is possible to effectively remove the solid crosslinking, since an autoclave or the like is necessary or solution boils under a normal pressure, it is not advantageous from the point of view of industry.

The acicular hematite particles heat-treated in the aqueous alkali suspension are, thereafter, filtered out and washed with water by an ordinary method so as to remove the soluble sodium salt and soluble sulfate which are washed out of the interiors and the surfaces of the particles and the alkali such as sodium or the like adhered to the surfaces of the hematite particles in the process of heat-treatment with the aqueous alkali suspension, and then dried.

As the method of washing the particles with water, a method generally industrially used such as a decantation method, a dilution method using a filter thickener and a method of passing water into a filter press is adopted.

If the soluble sodium salt and soluble sulfate which are contained within the high-density hematite particles are washed out with water, even if soluble sodium salt and soluble sulfate adhere to the surfaces when the surfaces of the hematite particles are coated with a coating material in a subsequent step, for example, the later-described coating step, they can be easily removed by water-washing.

Alternatively, the high-density acicular hematite particles coated with the oxide of tin or the oxides of tin and antimony may be produced by the following method. That is, by using acicular goethite particles uncoated with the hydroxide of tin or the hydroxides of tin and antimony but coated with the sintering-preventive agent solely as a starting material, high-density acicular hematite particles uncoated with the hydroxide of tin or the hydroxides of tin and antimony are first produced. The obtained high-density acicular hematite particles are heated in an aqueous alkaline solution, and then filtered and washed with water by ordinary methods. Next, the thus treated high-density acicular hematite particles are coated with the hydroxide of tin or the hydroxides of tin and antimony in the same manner as the above-mentioned coating-treatment of the acicular goethite particles. Thereafter, the high-density acicular hematite particles coated with the hydroxide of tin or the hydroxides of tin and antimony are heated at a temperature of usually not less than 300° C., preferably 350 to 850° C., to convert the hydroxide of tin or the hydroxides of tin and antimony on surfaces of the high-density acicular hematite particles, into the oxide of tin or the oxides of tin and antimony, thereby obtaining the high-density acicular hematite particles coated with the oxide of tin or the oxides of tin and antimony.

The high-density acicular hematite particles coated with the oxide of tin or the oxides of tin and antimony according to the present invention, may be further coated with at least one compound selected from the group consisting of a hydroxide of aluminum, an oxide of aluminum, a hydroxide of silicon and an oxide of silicon, if required.

In the coating-treatment, an aluminum compound, a silicon compound or both the aluminum and silicon compounds are added to a water suspension obtained by dispersing the high-density acicular hematite particles coated with the oxide of tin or the oxides of tin and antimony in an aqueous solution. The suspension is stirred and if required, the pH value of the suspension is adjusted properly to coat at least a part of the surface of the high-density acicular hematite particles with the hydroxide of aluminum, the oxide of aluminum, the hydroxide of silicon or the oxide of silicon. The suspension is then filtered to separate the coated high-density acicular hematite particles therefrom. The coated high-density acicular hematite particles is further washed with water, dried and pulverized. If required, the high-density acicular hematite particles may be subjected to deaeration, compaction or other treatments.

As the aluminum compound for the coating, the same aluminum compounds as those described above as the sintering preventive are usable.

The amount of aluminum compound added is usually 0.01 to 50.00 wt % (calculated as Al) based on the weight of the acicular hematite particles. When the amount is less than 0.01 wt %, the improvement of the dispersibility in the vehicle may be insufficient. On the other hand, if the amount exceeds 50.00 wt %, the coating effect becomes saturated, so that it is meaningless to add an aluminum compound more than necessary.

As the silicon compound, the same silicon compounds as those described above as the sintering preventive are usable.

The amount of silicon compound added is usually 0.01 to 50.00 wt % (calculated as SiO₂) based on the weight of the acicular hematite particles. When the amount is less than 0.01 wt %, the improvement of the dispersibility in the vehicle may be insufficient. On the other hand, when the amount exceeds 50.00 wt %, the coating effect becomes saturated, so that it is meaningless to add an silicon compound more than necessary.

When both an aluminum compound and a silicon compound are used, the amount of thereof used is preferably 0.01 to 50.00 wt % (calculated as Al and SiO₂) based on the weight of the acicular hematite particles.

It is important in the present invention that when the high-purity and high-density acicular hematite particles in which at least a part of the surface of the particle is coated with an oxide of tin or oxides of tin and antimony, and, which have an average major axial diameter of not more than 0.3 μm, a pH value of not less than 8, and which contain soluble sodium salts of not more than 300 ppm soluble sodium (calculated as Na) and soluble sulfates of not more than 150 ppm soluble sulfate (calculated as SO₄), are used as the non-magnetic particles for a non-magnetic undercoat layer, it is possible to enhance the strength and the surface smoothness of the non-magnetic undercoat layer owing to the excellent dispersibility of the high-purity and high-density acicular hematite particles into a binder resin; and that when a magnetic recording medium is formed by using the non-magnetic undercoat layer, it is possible to reduce the light transmittance and the surface resistivity, to enhance the strength and to make the surface of the magnetic recording layer more smooth. Further, it is possible to suppress the deterioration in the magnetic properties which is caused by the corrosion of the acicular magnetic particles containing iron as a main ingredient dispersed in the magnetic recording layer.

The reason why the strength of the non-magnetic undercoat layer is enhanced and the surface of the non-magnetic undercoat layer is made more smooth, is considered to be as follows. Since it is possible to sufficiently remove the soluble sodium and the soluble sulfate, which agglomerate hematite particles by firmly crosslinking, by washing the particles with water, the agglomerates are separated into substantially discrete particles, so that acicular hematite particles having an excellent dispersion in the vehicle are obtained.

This fact will be explained in the following. The goethite particles as the starting material are produced by various methods, as described above. When as the raw material for producing acicular goethite particles ferrous sulfate is used in any method, a large amount of sulfate [SO₄ ²⁻] naturally exists in the goethite suspension.

Especially, when goethite particles are produced from an acidic solution, since water-soluble sulfate such as Na₂SO₄ is simultaneously produced and an alkali metal such as K⁺, NH₄ ⁺ and Na⁺ are contained in the goethite suspension, a deposit containing an alkali metal and a sulfate is easily produced. This deposit is represented by RFe₃(SO₄) (OH)₆, (R=K⁺, NH₄ ⁺, or Na⁺). Such a deposit is a slightly soluble sulfuric acid-containing salt and cannot be removed by an ordinary water-washing method. This slightly soluble salt becomes a soluble sodium salt or a soluble sulfate in the next heat-treatment step. The soluble sodium salt and soluble sulfate are firmly combined with the interiors or the surfaces of the acicular hematite particles by a sintering preventive, which is essential for preventing the deformation of the acicular hematite particles and sintering between particles in the heat-treatment at a high temperature for the densification of the particles and which is crosslinking the acicular hematite particles. In this manner, agglomeration between acicular hematite particles becomes further firmer. As a result, the soluble sulfate and the soluble sodium salt, especially, imprisoned in the interiors of the particles or the agglomerates become very difficult to remove by an ordinary water-washing method.

When acicular goethite particles are produced in an aqueous alkali solution by using ferrous sulfate and sodium hydroxide, Na₂SO₄ is simultaneously produced as a sulfate and NaOH exists in the goethite suspension. Since they are both soluble, if the acicular goethite particles are adequately washed with water, Na₂SO₄ and NaOH ought to be removed. However, since the crystallinity of acicular goethite particles is generally small, the water-washing effect is poor, and when the particles are washed with water by an ordinary method, the particles still contain water-soluble contents such as a soluble sulfate [SO₄ ²⁻] and a soluble sodium salt [Na⁺]. The water-soluble contents are firmly combined with the interiors or the surfaces of the acicular hematite particles by the sintering preventive which is crosslinking the particles, as described above, and the agglomeration between acicular hematite particles becomes further firmer. As a result, the soluble sulfate and the soluble sodium salt, especially, imprisoned in the interiors of the particles or the agglomerates become very difficult to remove by an ordinary water-washing method.

It is considered that when the high-density acicular hematite particles in which the soluble sodium salt and the soluble sulfate are firmly combined with the interiors or the surfaces of the particles via the soluble sintering preventive, as described above, are pulverized by a wet-process so as to deagglomerate coarse particles, and heat-treated in the aqueous alkali solution having a pH value of not less than 13 at a temperature of not less than 80° C., the aqueous alkali solution sufficiently permeates into the interiors of the hematite particles, so that the binding strength of the sintering preventive which is firmly combined with the interiors and the surfaces of the particles, and the interiors of the agglomerates is gradually weakened, and the crosslinking is dissociated from the interiors and the surfaces of the particles and the interiors of the agglomerates, and simultaneously, the water-soluble sodium salt and the water-soluble sulfate are easily removed by water-washing.

It is considered that the deterioration in the magnetic properties which is caused by the corrosion of the acicular magnetic particles containing iron as a main ingredient, which are dispersed in the magnetic recording layer is suppressed because the contents of the soluble sodium salt and the soluble sulfate, which accelerate the corrosion of a metal, in the acicular hematite particles are small and the pH value of the hematite particles themselves is as high as not less than 8.

Actually, it is confirmed that a progress of corrosion of acicular magnetic particles containing iron as a main ingredient was suppressed by a synergistic effect of a small soluble content and a pH value of not less than 8, from the fact that the advantages of the present invention was not attained in any of the cases of (i) heat-treating the hematite particles after wet-pulverization in a slurry with the pH value adjusted to less than 13 at a temperature of not less than 80° C., (ii) heat-treating the hematite particles in a slurry with the pH value adjusted to not less than 13 at a temperature of less than 80° C., or (iii) heat-treating the hematite particles containing coarse particles without being pulverized by a wet-process in a slurry with the pH value adjusted to not less than 13 at a temperature of not less than 80° C., as shown in later-described examples and comparative examples.

By using the high-density acicular hematite particles according to the present invention, a non-magnetic undercoat layer having an excellent surface smoothness and a uniform thickness because of their excellent dispersibility in vehicle, as described above, can be obtained, and a mechanical strength of a substrate when the non-magnetic undercoat layer is formed thereon can be improved. Accordingly, the high-density acicular hematite particles according to the present invention can be suitably used as non-magnetic particles for non-magnetic undercoat layer.

Further, by using the non-magnetic undercoat layer according to the present invention, it becomes possible to form thereon a magnetic recording layer having an excellent surface smoothness and a uniform thickness due to its excellent properties described above. Accordingly, the non-magnetic undercoat layer according to the present invention can be suitably used as a non-magnetic undercoat layer of a magnetic recording medium for high-density recording.

Furthermore, the magnetic recording medium according to the present invention can exhibit a low transmittance and a low surface resistivity, because the high-density acicular hematite particles used therein have an excellent dispersibility in vehicle, and are coated with an oxide of tin or oxides of tin and antimony. In addition, since the high-density acicular hematite particles have a less soluble sodium salt content, a less soluble sulfate content and a pH value of not less than 8, acicular magnetic particles containing iron as a main ingredient, dispersed in a magnetic recording layer of the magnetic recording medium, can be prevented from being corroded, thereby inhibiting the deterioration in magnetic properties of the magnetic recording layer. Accordingly, the magnetic recording medium according to the present invention can maintain its excellent properties for a long period of time.

EXAMPLES

The present invention is described in more detail by Examples and Comparative Examples, but the Examples are only illustrative and, therefore, not intended to limit the scope of this invention.

Various properties of the high-density acicular particles, non-magnetic undercoat layer and magnetic recording medium according to the present invention were evaluated by the following methods.

(1) The residue on sieve after the wet-pulverization was obtained by measuring the concentration of the slurry after pulverization by a wet-process in advance, and determining the quantity of the solid content on the sieve remaining after the slurry equivalent to 100 g of the solid content was passed through the sieve of 325 meshes (mesh size: 44 μm).

(2) The average major axial diameter and the average minor axial diameter of the particles are expressed by the average values of 350 particles measured in the photograph obtained by magnifying an electron micrograph (×30000) by 4 times in the vertical and horizontal directions, respectively. The aspect ratio is the ratio of the average major axial diameter and the average minor axial diameter.

(3) The geometrical standard deviation (σg) of particle size distribution of the major axial diameter was obtained by the following method. The major axial diameters of the particles were measured from the magnified electron microphotograph in the above-mentioned (2). The actual major axial diameters of the particles and the number of particles were obtained from the calculation on the basis of the measured values. On logarithmico-normal probability paper, the major axial diameters were plotted at regular intervals on the abscissa-axis and the accumulative number of particles belonging to each interval of the major axial diameters was plotted by percentage on the ordinate-axis by a statistical technique. The major axial diameters corresponding to the number of particles of 50% and 84.13%, respectively, were read from the graph, and the geometrical standard deviation (σg) was measured from the following formula:

Geometrical standard deviation (σg)={major axial diameter (μm) corresponding to 84.13% under integration sieve}/{major axial diameter (geometrical average diameter) corresponding to 50% under integration sieve}.

The smaller the geometrical standard deviation, the more excellent the particle size distribution of the major axial diameters of the particles.

(4) The specific surface area is expressed by the value measured by a BET method.

(5) The decree of denseness of the particles is represented by S_(BET)/S_(TEM) as described above. The S_(BET) is a specific surface area measured by the above-described BET method. The S_(TEM) is a value calculated from the average major axial diameter d cm and the average minor axial diameter w cm measured from the electron microphotograph described in (2) on the assumption that a particle is a rectangular parallellopiped in accordance with the following formula:

S _(TEM) (m ² /g)={(4·d·w+2w ²)/(d·w ²·ρ_(p))}×10⁻⁴

wherein ρ_(p) is the true specific gravity of the hematite particles, and 5.2 g/cm³ was used.

Since S_(TEM) is a specific surface area of a particle having a smooth surface without any dehydration pore within or on the surface thereof, the closer S_(BET)/S_(TEM) of particles is to 1, it means, the smoother surface the particles have without any dehydration pore within or in the surface thereof, in other words, the particles are high-density particles.

(6) The content of each of Sn, Sb, Al, Co, P and Si was measured from fluorescent X-ray analysis.

(7) The pH value of the particles was measured in the following method. 5 g of the sample was weighed into a 300-ml triangle flask, and 100 ml of pure water was added. The suspension was heated and after keeping the boiled state for 5 minutes, it was corked and left to cool to an ordinary temperature. After adding pure water which was equivalent to the pure water lost by boiling, the flask was corked again, shaken for 1 minute, and left to stand for 5 minutes. The pH value of the supernatant obtained was measured in accordance JIS Z 8802-7.

(8) The contents of soluble sodium salts and soluble sulfates were measured by measuring the Na content and SO₄ ²⁻ content in the filtrate obtained by filtering the supernatant liquid produced for the measurement of pH value which is described above through filter paper No. 5C, by using an Inductively Coupled Plasma Emission Spectrophotometer (manufactured by Seiko Instruments and Electronics, Ltd.).

(9) The volume resistivity of acicular hematite particles was measured as follows. First, 0.5 g of acicular hematite particles were weighed and pressure-molded under 140 kg/cm² by KBr pellet molding apparatus (manufactured by Simazu Seisakusho Co., Ltd.) to form a cylindrical sample.

Next, the cylindrical sample was allowed to stand at a temperature of 25° C. and a relative humidity (RH) of 60% for not less than 12 hours. The sample was set between stainless steel electrodes, and impressed with a voltage of 15 V using a Wheatstone bridge “TYPE 2768” (manufactured by Yokogawa Hokushin Denki Co., Ltd.) to measure a resistance (Ω) thereof.

Next, the sample was measured for a upper surface area A (cm²) and a thickness t (cm) thereof. A volume resistivity X (Ω·cm) is obtained by the following formula:

X (Ω·cm)=R×(A/t)

wherein R represents an actual measured value of resistance.

(10) The surface resistivity of a coating film was measured as follows. The coating film was first allowed to stand at a temperature of 25° C. and a relative humidity (RH) of 60% for not less than 12 hours. Thereafter, the coating film which was slit into a width of 6 mm, and was disposed between metal electrodes each having a width of 6.5 mm, such that a coating surface of the coating film was contacted with these electrodes. 170 g of weights were respectively fixed to opposite ends of the coating film so as to bring the coating surface of the coating film into close contact with the electrodes. Thereafter, D.C. voltage of 500 V was applied between the metal electrodes to measure a surface resistivity of the coating film by using a resistance meter Model 14329A (manufactured by Yokogawa Hewlett Packard Co., Ltd.).

(11) The viscosity of the coating composition was obtained by measuring the viscosity of the coating composition at 25° C. at a shear rate D of 1.92 sec⁻¹ by using an E type viscometer EMD-R (manufactured by Tokyo Keiki, Co., Ltd.).

(12) The gloss of the surface of the coating film of each of the non-magnetic undercoat layer and the magnetic recording layer was measured at an angle of incidence of 45° by a glossmeter UGV-5D (manufactured by Suga Shikenki, Co., Ltd.).

(13) The surface roughness Ra is expressed by the average value of the center-line average roughness of the profile curve of the surface of the coating film by using “Surfcom-575A” (manufactured by Tokyo Seimitsu Co., Ltd.).

(14) The strength of the non-magnetic undercoat layer and magnetic recording medium was expressed the Young's modulus obtained by “Autograph” (produced by Shimazu Seisakusho Ltd.). The Young's modulus was expressed by the ratio of the Young's modulus of the coating film to that of a commercially available video tape “AV T-120” (produce by Victor Company of Japan, Ltd.). The higher the relative value, the more favorable.

(15) The magnetic properties were measured under an external magnetic field of 10 kOe by “Vibration Sample Magnetometer VSM-3S-15” (manufactured by Toei Kogyo, Co., Ltd.).

(16) The change in the magnetic properties with passage of time of a magnetic recording medium caused by the corrosion of the magnetic particles containing iron as a main ingredient was examined as follows.

The magnetic recording medium was allowed to stand in an environment of a temperature of 60° C. and a relative humidity of 90% for 14 days, and the coercive force and the saturation magnetic flux density were measured before and after standing. A change in each characteristic was divided by the value before standing, and represented by percentage as a percentage of change.

(17) The light transmittance of a magnetic recording medium is expressed by the linear adsorption coefficient using a light transmittance at λ=900 nm measured by “Photoelectric Spectrophotometer UV-2100” (manufactured by Shimazu Seisakusho, Ltd.). The linear adsorption coefficient is defined by the following formula:

Linear adsorption coefficient (μm⁻¹)={1n (1/t)}/FT

wherein t represents light transmittance (−) at λ=900 nm, and FT represents thickness (μm) of the coating film composition of the film used for the measurement.

The larger the value, the more difficult it is for the magnetic recording medium to transmit light.

As a blank for measuring the linear adsorption coefficient, the same non-magnetic substrate as that of the above-mentioned magnetic recording medium, was used.

(18) The thickness of each of the non-magnetic substrate, the non-magnetic undercoat layer and the magnetic recording layer constituting the magnetic recording medium was measured in the following manner by using a Digital Electronic Micrometer K351C (manufactured by Anritsu Denki Corp.)

The thickness (A) of a non-magnetic substrate was first measured. Similarly, the thickness (B) (B=the sum of the thicknesses of the non-magnetic substrate and the non-magnetic undercoat layer) of a substrate obtained by forming a non-magnetic undercoat layer on the non-magnetic substrate was measured. Furthermore, the thickness (C) (C=the sum of the thicknesses of the non-magnetic substrate, the non-magnetic undercoat layer and the magnetic recording layer) of a magnetic recording medium obtained by forming a magnetic recording layer on the non-magnetic undercoat layer was measured. The thickness of the non-magnetic undercoat layer is expressed by B−A, and the thickness of the magnetic recording layer is expressed by C−B.

Example 1

<production of acicular hematite particles>

Example 1

1,200 g of spindle-shaped goethite particles obtained by the afore-mentioned goethite production method (B) (average major axial diameter: 0.178 μm, average minor axial diameter: 0.0225 μm, aspect ratio: 7.91:1, BET specific surface area: 160.3 m²/g, soluble sodium salt content: 1232 ppm (calculated as Na), soluble sulfate content: 621 ppm (calculated as SO₄), pH value: 6.7 and geometrical standard deviation: 1.33) were suspended in a mixed solution of an aqueous ferrous sulfate solution and an aqueous sodium carbonate solution to form a slurry having a solid content of 8 g/liter. After 150 liters of the slurry was heated to 60° C., a 0.1N NaOH aqueous solution was added thereto to adjust the pH value to 9.0.

Next, 2,022 ml of an aqueous solution containing 0.5 mol/liter of sodium stannate was gradually added to the thus obtained alkaline slurry. After completion of the addition, a 0.8N acetic acid solution was added to the slurry to adjust the pH value to 7.5. Thereafter, the slurry was successively filtered, washed with water, dried and pulverized by ordinary methods to obtain spindle-shaped goethite particles whose surfaces were coated with a hydroxide of tin. It was confirmed that the amount of the hydroxide of tin was 9.32% by weight (calculated as Sn) based on the weight of the spindle-shaped goethite particles.

1,000 g of the thus obtained spindle-shaped goethite particles coated with the hydroxide of tin, were charged into a stainless steel rotary furnace, and heat-dehydrated in air at 350° C. for 60 minutes while rotating the furnace, thereby obtaining low-density spindle-shaped hematite particles coated with an oxide of tin. It was determined that the thus obtained low-density spindle-shaped hematite particles had an average major axial diameter of 0.134 μm, an average minor axial diameter of 0.0194 μm, an aspect ratio (average major axial diameter/average minor axial diameter) of 6.91:1, a BET specific surface area (S_(BET)) of 168.3 m²/g, a degree of densification (S_(BET)/S_(TEM)) of 3.96, a soluble sodium salt content of 1123 ppm (calculated as Na), a soluble sulfate content of 465 ppm (calculated as SO₄), a pH value of 6.3, a geometrical standard deviation of 1.34 and a volume resistivity of 1.1×10⁶ Ωcm. Further, the amount of the oxide of tin was 10.60% by weight (calculated as Sn) based on the weight of the spindle-shaped hematite particles.

Next, 900 g of the low-density spindle-shaped hematite particles were charged into a ceramic rotary furnace, and heated in air at 650° C. for 20 minutes while rotating the furnace to seal dehydrating pores of the particles, thereby obtaining high-density spindle-shaped hematite particles coated with the oxide of tin. It was determined that the obtained high-density spindle-shaped hematite particles had an average major axial diameter of 0.129 μm, an average minor axial diameter of 0.0206 μm, an aspect ratio (average major axial diameter/average minor axial diameter) of 6.26:1, a BET specific surface area (S_(BET)) of 46.6 m²/g, a degree of high densification (S_(BET)/S_(TEM)) of 1.16, a soluble sodium salt content of 2864 ppm (calculated as Na), a soluble sulfate content of 2956 ppm (calculated as SO₄), a pH value of 5.4, a geometrical standard deviation of 1.36 and a volume resistivity of 9.6×10⁵ Ωcm. Further, the amount of the oxide of tin was 10.72% by weight (calculated as Sn) based on the weight of the spindle-shaped hematite particles.

After 800 g of the high-density spindle-shaped hematite particles obtained were roughly pulverized by a Nara mill in advance, the obtained particles were charged into 4.7 liters of pure water and peptized by a homomixer (manufactured by Tokushu-kika Kogyo, CO., Ltd.) for 60 minutes.

The slurry of the high-density spindle-shaped hematite particles obtained was then mixed and dispersed for 3 hours at an axial rotation frequency of 2000 rpm while being circulated by a horizontal SGM (Dispermat SL, manufactured by S. C. Adichem, CO., Ltd.). The spindle-shaped hematite particles in the slurry remaining on a sieve of 325 meshes (mesh size: 44 μm) was 0% by weight.

The concentration of the high-density spindle-shaped hematite particles in the slurry was adjusted to 100 g/liter, and a 6N-aqueous NaOH solution was added to 7 liter of the slurry under stirring so as to adjust the pH value to 13.3. The slurry was then heated to 95° C. under stirring, and was held for 3 hours at 95° C.

The slurry was then washed with water by a decantation method and the pH value of the slurry was adjusted to 10.5. When the concentration of the slurry at this point was checked so as to ensure the accuracy, it was 96 g/liter.

2 liter of the slurry washed with water was filtered through a Buchner filter, and pure water was passed until the electric conductivity of the filtrate became not more than 30 μs. The particles were then dried by an ordinary method and pulverized so as to obtain the target high-density spindle-shaped hematite particles. The high-density spindle-shaped hematite particles obtained contained 10.83 wt % of an oxide of tin (calculated as Sn), and had an average major axial diameter of 0.128 μm, a minor axial diameter of 0.0206 μm, an aspect ratio of 6.71:1, a geometric standard deviation σg of particle size (major axial diameter) of 1.35, a BET specific surface (S_(BET)) of 47.1 m²/g, a S_(BET)/S_(TEM) value of densification of 1.17 and a pH value of the particles of 8.9. The spindle-shaped hematite particles contained soluble sodium salts of 112 ppm soluble sodium (calculated as Na) and soluble sulfates of 41 ppm soluble sulfate (calculated as SO₄). The volume resistivity thereof was 6.3×10⁶ Ωcm.

Example 2

<Production of a non-magnetic undercoat layer>

12 g of the high-density spindle-shaped hematite particles obtained in the Example 1 were mixed with a binder resin solution (30 wt % of vinyl chloride-vinyl acetate copolymer resin having a sodium sulfonate group and 70 wt % of cyclohexanone) and cyclohexanone, and the mixture (solid content: 72 wt %) obtained was kneaded by a plasto-mill for 30 minutes.

The thus-obtained kneaded material was charged into a 140 ml-glass bottle together with 95 g of 1.5 mmφ glass beads, a binder resin solution (30 wt % of polyurethane resin having a sodium sulfonate group and 70 wt % of a solvent (methyl ethyl ketone:toluene=1:1)), cyclohexanone, methyl ethyl ketone and toluene, and the obtained mixture was mixed and dispersed by a paint shaker for 6 hours to obtain a coating composition.

The thus-obtained coating composition containing high-density spindle-shaped hematite particles was as follows:

High-density spindle-shaped 100 parts by weight hematite particles Vinyl chloride-vinyl acetate 10 parts by weight copolymer resin having a sodium sulfonate group Polyurethane resin having a 10 parts by weight sodium sulfonate group Cyclohexanone 44.6 parts by weight Methylethyl ketone 111.4 parts by weight Toluene 66.9 parts by weight

The coating composition obtained containing high-density spindle-shaped hematite particles was applied to a polyethylene terephthalate film of 12 μm thick to a thickness of 55 μm by an applicator, and the film was then dried, thereby forming a non-magnetic undercoat layer. The thickness of the non-magnetic undercoat layer was 3.5 μm.

The gloss of the coating film of the obtained non-magnetic undercoat layer was 201%, the surface roughness Ra was 6.8 nm, and the Young's modulus (relative value) was 128.

Example 3

<Production of a magnetic recording layer>

12 g of spindle-shaped magnetic particles containing iron as a main ingredient (average major axial diameter: 0.104 μm, average minor axial diameter: 0.0158 μm, aspect ratio: 6.58:1, coercive force: 1905 Oe, saturation magnetization: 138 emu/g, Al content: 4.41 wt %, and Co content: 5.51 wt %), 1.2 g of a polishing agent (AKP-50: trade name, produced by Sumitomo Chemical Co., Ltd.), 0.36 g of carbon black (#3250B, trade name, produced by Mitsubishi Chemical Corp.), a binder resin solution (30 wt % of vinyl chloride-vinyl acetate copolymer resin having a sodium sulfonate group and 70 wt % of cyclohexanone) and cyclohexanone were mixed to obtain a mixture (solid content: 78 wt %). The mixture was further kneaded by a plasto-mill for 30 minutes to obtain a kneaded material.

The thus-obtained kneaded material was charged into a 140 ml-glass bottle together with 95 g of 1.5 mmφ glass beads, a binder resin solution (30 wt % of polyurethane resin having a sodium sulfonate group and 70 wt % of a solvent (methyl ethyl ketone:toluene=1:1)), cyclohexanone, methyl ethyl ketone and toluene, and the mixture was mixed and dispersed by a paint shaker for 6 hours. Thereafter, the lubricant and hardening agent were added to the resultant mixture, and then the obtained mixture was mixed and dispersed by paint shaker for 15 minutes.

The thus-obtained magnetic coating composition was as follows:

Magnetic particles containing 100 parts by weight iron as a main ingredient Vinyl chloride-vinyl acetate 10 parts by weight copolymer resin having a sodium sulfonate group Polyurethane resin having a 10 parts by weight sodium sulfonate group Polishing agent (AKP-50) 10 parts by weight Carbon black (#3250B) 3.0 parts by weight Lubricant (myristic acid: butyl 3.0 parts by weight stearate 1:2) Hardening agent (polyisocyanate) 5.0 parts by weight Cyclohexanone 65.8 parts by weight Methyl ethyl ketone 164.5 parts by weight Toluene 98.7 parts by weight

The magnetic coating composition obtained was applied to the non-magnetic undercoat layer to a thickness of 15 μm by an applicator, and the magnetic recording medium obtained was oriented and dried in a magnetic field, and then calendered. The magnetic recording medium was then subjected to a curing reaction at 60° C. for 24 hours, and thereafter slit into a width of 0.5 inch, thereby obtaining a magnetic tape. The thickness of the magnetic recording layer was 1.1 μm.

The magnetic tape obtained had a coercive force of 1986 Oe, a squareness (Br/Bm) of 0.87, a gloss of 228%, a surface roughness Ra of 6.4 nm, a Young's modulus (relative value) of 133, a linear absorption coefficient of 1.21, a surface resistivity of 1.1×10⁷ Ω/sq. The changes in the coercive force and the saturation magnetic flux density Bm with passage of time were 6.4%, and 5.4%, respectively.

Examples 4 to 21, Comparative Examples 1 to 14

<Types of acicular goethite particles>

The starting materials A to F shown in Table 1 were used as the starting materials for producing acicular hematite particles.

<Production of low-density acicular hematite articles>

Low-density acicular hematite particles were obtained in the same way as in Example 1 except for varying the kind of acicular goethite particles as the starting materials, the kind and amount of tin compound, the kind and amount of antimony compound, the kind and amount of sintering preventive, and heat-dehydrating temperature and time.

The main producing conditions and various properties are shown in Tables 2 to 3.

Examples 22 to 39. Comparative Examples 15 to 27

<Production of high-density acicular hematite particles>

High-density acicular hematite particles were obtained in the same way as in Example 1 except for varying the kind of low-density hematite particles, and the heating temperature and time for densification.

The main producing conditions and various properties are shown in Tables 4 and 5.

Examples 40 to 57, Comparative Examples 28 to 35

<Treatment of acicular hematite particles in an aqueous alkali solution>

High-purity, high-density acicular hematite particles were obtained in the same way as in Example 1 except for varying the kind of high-density acicular hematite particles, whether or not the wet-pulverization process was conduced, whether or not the heat-treatment in the aqueous alkali solution was conducted, the pH value of the slurry, and the heating time and temperature.

The main producing conditions and various properties are shown in Tables 6 to 9.

Example 58

<Surface coating of acicular hematite particles>

The concentration of the slurry having a pH value 10.5 which was obtained in Example 40 by washing the particles in an aqueous alkali solution after heat-treatment with water by a decantation method was 96 g/liter. 5 liter of the slurry was re-heated to 60° C., and 231 ml (equivalent to 1.3 wt % (calculated as Al) based on the acicular hematite particles) of a 1.0-N NaAlO₂ solution was added to the slurry, and the mixture was held for 60 minutes. Thereafter, the pH value of the mixture was adjusted to 8.2 by using acetic acid. The particles were then filtered out, washed with water, dried and pulverized in the same way as in Example 1, thereby obtaining acicular hematite particles coated with a coating material.

The main producing conditions and various properties are shown in Tables 10 and 11.

Examples 59 to 72

Acicular hematite particles coated with a coating material were obtained in the same way as in Example 58 except for varying the kind of acicular hematite particles, and the kind and the amount of surface treating material.

The main producing conditions and various properties are shown in Table 10 and 11.

Example 73

<Coating-treatment of high-density acicular hematite particles treated with alkaline aqueous solution, with oxide of tin or oxides of tin and antimony>

The slurry obtained in Example 55 by washing with water by a decantation method after the heat-treatment in alkaline aqueous solution, had a pH value of 10.5 and a concentration of 96 g/liter. After 5 liters of the slurry was heated again to 60° C., 121 ml of a 1.0-mol sodium stannate solution (corresponding to 3.0% by weight (calculated as Sn) based on the weight of the acicular hematite particles) was added thereto. After the slurry was allowed to stand for 60 minutes, the pH value thereof was adjusted to 8.0 by adding acetic acid thereto. Next, the slurry was filtered to separate a solid component therefrom, and then the solid component was washed with water, dried and pulverized in the same manner as in Example 1, thereby obtaining high-density acicular hematite particles coated with a hydroxide of tin.

The essential production conditions and properties of the obtained high-density acicular hematite particles are shown in Tables 10 and 11.

Examples 74 and 75

The same procedure as defined in Example 73 was conducted except that kind of acicular hematite particles treated with alkaline aqueous solution, kind and amount of tin compound, kind, amount and use or non-use of antimony compound and treating temperature and treating time used for the heat-treatment were varied, thereby obtaining high-density acicular hematite particles coated with a hydroxide of tin or hydroxides of tin and antimony.

The essential production conditions and properties of the obtained high-density acicular hematite particles are shown in Tables 10 and 11.

Example 76

The high-density acicular hematite particles coated with the hydroxide of tin which were obtained in Example 73, were charged into a stainless steel rotary furnace, and heated in air at 400° C. for 60 minutes while rotating the furnace, thereby obtaining high-density acicular hematite particles coated with an oxide of tin.

The essential production conditions and properties of the obtained high-density acicular hematite particles are shown in Tables 12 and 13.

Examples 77 and 78

The same procedure as defined in Example 76 was conducted except that kind of high-density acicular hematite particles coated with a hydroxide of tin or hydroxides of tin and antimony and treating temperature and treating time used for the heat-treatment were varied, thereby obtaining high-density acicular hematite particles coated with an oxide of tin or oxides of tin and antimony.

The essential production conditions and properties of the obtained high-density acicular hematite particles are shown in Tables 12 and 13.

Examples 79 to 111, Comparative Examples 36 to 50

<Production of a non-magnetic undercoat layer>

A non-magnetic undercoat layer was obtained in the same way as in Example 2 by using the acicular hematite particles obtained in Examples 40 to 54, 58 to 72 and 76 to 78, Comparative Examples 1, 3, 15 to 18, 23 and 28 to 35.

The main producing conditions and various properties are shown in Tables 14 to 16.

Examples 112 to 144, Comparative Examples 51 to 65

<Production of a magnetic recording medium using magnetic particles containing iron as a main ingredient>

A magnetic recording medium using acicular magnetic particles containing iron as a main ingredient was obtained in the same way as in Example 3 except for varying the kind of non-magnetic undercoat layer obtained in Examples 79 to 111 and Comparative Examples 36 to 50 and the kind of acicular magnetic particles containing iron as a main ingredient.

The main producing conditions and various properties are shown in Tables 17 to 19.

TABLE 1 Acicular Goethite particles Kind of Average major Average minor starting Production axial axial material method diameter (μm) diameter (μm) Starting BB 0.181 0.0246 material A Starting BB 0.220 0.0283 material B Starting DD 0.245 0.0305 material C Starting CC 0.164 0.0218 material D Starting AA 0.260 0.0298 material E Starting BB 0.234 0.0288 material F Acicular Goethite particles Geometrical Kind of standard BET specific starting Aspect ratio* deviation σg surface area material (−) (−) (m²/g) Starting 7.36 1.37 151.0 material A Starting 7.77 1.34 125.0 material B Starting 8.03 1.31 95.1 material C Starting 7.52 1.37 186.5 material D Starting 8.72 1.44 72.6 material E Starting 8.13 1.31 110.5 material F Acicular Goethite particles Kind of Soluble starting sodium salt Soluble pH value material (ppm) sulfate (ppm) (−) Starting 412 386 6.8 material A Starting 512 264 7.2 material B Starting 1215 2150 5.1 material C Starting 415 915 5.5 material D Starting 1565 171 8.3 material E Starting 436 312 6.9 material F (Note) *: Aspect ratio = average major axial diameter/average minor axial diameter

(Note) PRODUCTION METHOD:

AA: A method of oxidizing a suspension having a pH value of not less than 11 and containing colloidal ferrous hydroxide particles which is obtained by adding not less than an equivalent of an alkali hydroxide solution to an aqueous ferrous salt solution, by passing an oxygen-containing gas thereinto at a temperature of not higher than 80° C.

BB: A method of producing acicular goethite particles by oxidizing a suspension containing FeCO₃ which is obtained by reacting an aqueous ferrous salt solution with an aqueous alkali carbonate solution, by passing an oxygen-containing gas thereinto after aging the suspension, if necessary.

CC: A method of growing acicular seed goethite particles by oxidizing a ferrous hydroxide solution containing colloidal ferrous hydroxide particles which is obtained by adding less than an equivalent of an alkali hydroxide solution or an alkali carbonate solution to an aqueous ferrous salt solution, by passing an oxygen-containing gas thereinto, thereby producing acicular seed goethite particles, adding not less than an equivalent of an alkali hydroxide solution to the Fe²⁺ in the aqueous ferrous salt solution, to the aqueous ferrous salt solution containing the acicular goethite seed particles, and passing an oxygen-containing gas into the aqueous ferrous salt solution.

DD: A method of growing acicular seed goethite particles by oxidizing a ferrous hydroxide solution containing colloidal ferrous hydroxide particles which is obtained by adding less than an equivalent of an alkali hydroxide solution or an alkali carbonate solution to an aqueous ferrous salt solution, by passing an oxygen-containing gas thereinto, thereby producing acicular seed goethite particles, and growing the obtained acicular seed goethite particles in an acidic or neutral region.

TABLE 2 Kind of acicular Sintering preventive goethite particles Calcu- Amount as the starting lated added Examples material Kind as (wt. %) Example 4 Particles of Sodium stannate Sn 15.0 Example 1 Example 5 Starting material A Stannous chloride Sn 20.0 Example 6 Starting material A Sodium stannate Sn 50.0 #3 Water glass SiO₂ 1.0 Example 7 Starting material B Sodium stannate Sn 1.2 Example 8 Starting material B Sodium stannate Sn 3.0 Example 9 Starting material C Stannous chloride Sn 10.0 Example 10 Starting material C Sodium stannate Sn 50.0 Example 11 Starting material D Sodium stannate Sn 200.0 Example 12 Starting material D Sodium stannate Sn 500.0 Example 13 Starting material E Stannous chloride Sn 100.0 Example 14 Starting material E Sodium stannate Sn 75.0 Phosphoric acid P 0.5 Example 15 Starting material F Sodium stannate Sn 50.0 Antimony Sb 5.0 chloride Example 16 Starting material F Sodium stannate Sn 10.0 Antimony acetate Sb 2.0 Example 17 Particles of Sodium stannate Sn 100.0 Example 1 Antimony sol Sb 10.0 #3 Water glass SiO₂ 1.5 Example 18 Particles of Stannous chloride Sn 300.0 Example 1 Antimony Sb 15.0 chloride Aluminum sulfate Al 1.0 Example 19 Starting material A Sodium P 1.5 hexameta- phosphate Example 20 Starting material A #3 Water glass SiO₂ 2.0 Example 21 Starting material A Phosphoric acid P 0.5 #3 Water glass SiO₂ 0.75 Low-density acicular hematite Heat treatment for low particles densification Average major Average minor Temperature Time axial diameter axial diameter Examples (° C.) (min) (μm) (μm) Example 4 300 90 0.138 0.0199 Example 5 350 30 0.143 0.0214 Example 6 330 120  0.140 0.0221 Example 7 280 30 0.180 0.0261 Example 8 300 60 0.183 0.0260 Example 9 330 120  0.200 0.0277 Example 10 350 90 0.206 0.0290 Example 11 380 60 0.138 0.0211 Example 12 400 30 0.140 0.0240 Example 13 380 60 0.218 0.0283 Example 14 380 90 0.213 0.0276 Example 15 350 60 0.191 0.0277 Example 16 375 60 0.192 0.0278 Example 17 310 240  0.142 0.0205 Example 18 350 180  0.145 0.0211 Example 19 330 60 0.141 0.0213 Example 20 310 90 0.141 0.0210 Example 21 350 120  0.144 0.0278 Low-density acicular hematite particles Geometrical standard Aspect ratio* S_(BET) S_(TEM) Examples deviation σg (−) (−) (m²/g) (m²/g) Example 4 1.33 6.93 169.1 41.4 Example 5 1.37 6.68 168.5 38.6 Example 6 1.38 6.33 160.8 37.6 Example 7 1.34 6.90 144.0 31.6 Example 8 1.34 7.04 135.9 31.7 Example 9 1.33 7.22 119.0 29.7 Example 10 1.32 7.10 125.1 28.4 Example 11 1.37 6.54 197.5 39.2 Example 12 1.40 5.83 213.5 34.8 Example 13 1.44 7.70 110.8 28.9 Example 14 1.44 7.72 103.6 29.7 Example 15 1.32 6.90 146.9 29.8 Example 16 1.32 6.91 138.5 29.7 Example 17 1.34 6.93 173.8 40.2 Example 18 1.34 6.87 180.6 39.1 Example 19 1.36 6.62 171.6 38.8 Example 20 1.36 6.71 178.8 39.4 Example 21 1.36 6.92 186.2 39.7 Low-density acicular hematite particles S_(BET)/S_(TEM) Soluble sodium Soluble sulfate pH value Examples (−) salt (ppm) (ppm) (−) Example 4 4.08 1263 680 7.8 Example 5 4.36 1897 879 7.1 Example 6 4.28 1835 980 8.1 Example 7 4.56  870 789 6.5 Example 8 4.29 1123 987 6.8 Example 9 4.01 2356 1234  6.3 Example 10 4.41 2987 1145  6.8 Example 11 5.03 3456 789 7.9 Example 12 6.14 4890 891 8.0 Example 13 3.83 2156 1348  6.5 Example 14 3.49 1768 1123  7.5 Example 15 4.93 1345 888 6.0 Example 16 4.67 1879 1334  6.1 Example 17 4.32 2350 1345  8.1 Example 18 4.62 2879 789 7.3 Example 19 4.42 2006 912 7.5 Example 20 4.54 2128 986 7.3 Example 21 4.70 2166 982 7.3 (Note) *: Aspect ratio = average major axial diameter/average minor axial diameter

TABLE 3 Kind of Sintering preventive acicular goethite Calcu- Amount Comparative particles as the lated added Examples starting particles Kind as (wt. %) Comparative Particles of — — — Example 1 Example 1 Comparative Particles of — — — Example 2 Example 1 Comparative Particles of #3 Water glass SiO₂ 0.50 Example 3 Example 1 Comparative Particles of Phosphoric acid P 0.50 Example 4 Example 1 Comparative Particles of #3 Water glass SiO₂ 1.00 Example 5 Example 1 Comparative Particles of Sodium P 0.50 Example 6 Example 1 hexameta- phosphate Comparative Particles of #3 Water glass SiO₂ 1.50 Example 7 Example 1 Comparative Particles of #3 Water glass SiO₂ 0.20 Example 8 Example 1 Comparative Particles of Phosphoric acid P 0.75 Example 9 Example 1 Comparative Starting material F Sodium P 2.00 Example 10 hexameta- phosphate Comparative Starting material F #3 Water glass SiO₂ 1.25 Example 11 Comparative Starting material F Phosphoric acid P 1.50 Example 12 Comparative Starting material F Colloidal silica SiO₂ 0.25 Example 13 Comparative Starting material F Sodium stannate Sn 0.05 Example 14 Low-density acicular hematite Heat treatment for low particles densification Average major Average minor Comparative Temperature Time axial diameter axial diameter Examples (° C.) (min) (μm) (μm) Comparative 350 90 0.135 0.0199 Example 1 Comparative 380 45 0.132 0.0206 Example 2 Comparative 340 75 0.136 0.0197 Example 3 Comparative — — — — Example 4 Comparative 350 60 0.134 0.0199 Example 5 Comparative 350 30 0.132 0.0197 Example 6 Comparative 330 90 0.134 0.0197 Example 7 Comparative 300 60 0.132 0.0190 Example 8 Comparative 380 20 0.132 0.0195 Example 9 Comparative 380 90 0.193 0.0276 Example 10 Comparative 350 90 0.193 0.0280 Example 11 Comparative 330 30 0.192 0.0278 Example 12 Comparative 325 45 0.189 0.0288 Example 13 Comparative 300 60 0.185 0.0293 Example 14 Low-density acicular hematite particles Geometrical Comparative standard Aspect ratio* S_(BET) S_(TEM) Examples deviation σg (−) (−) (m²/g) (m²/g) Comparative 1.33 6.78 171.6 41.5 Example 1 Comparative 1.34 6.41 135.8 40.3 Example 2 Comparative 1.33 6.90 165.8 41.9 Example 3 Comparative — — — — Example 4 Comparative 1.34 6.73 134.8 41.5 Example 5 Comparative 1.35 6.70 125.9 42.0 Example 6 Comparative 1.35 6.80 145.0 41.9 Example 7 Comparative 1.35 6.95 145.9 43.4 Example 8 Comparative 1.36 6.77 156.9 42.4 Example 9 Comparative 1.33 6.99 124.3 29.9 Example 10 Comparative 1.33 6.89 131.2 29.5 Example 11 Comparative 1.32 6.91 138.2 29.7 Example 12 Comparative 1.33 6.56 136.3 28.7 Example 13 Comparative 1.32 6.31 126.4 28.3 Example 14 Low-density acicular hematite particles Soluble Soluble Volume Comparative S_(BET)/S_(TEM) sodium salt sulfate pH value resistivity Examples (−) (ppm) (ppm) (−) (Ωcm) Comparative 4.13  852 568 6.0 1.2 × 10⁸ Example 1 Comparative 3.37  903 498 6.5 — Example 2 Comparative 3.96 1245 423 6.8 4.0 × 10⁸ Example 3 Comparative — — — — — Example 4 Comparative 3.25 1235 568 6.7 — Example 5 Comparative 3.00 1025 612 6.6 — Example 6 Comparative 3.46 1365 682 7.1 — Example 7 Comparative 3.36 1265 591 7.2 — Example 8 Comparative 3.70 1124 654 7.1 — Example 9 Comparative 4.16 1026 689 6.9 — Example 10 Comparative 4.45 1176 563 7.1 — Example 11 Comparative 4.66 1015 597 7.0 — Example 12 Comparative 4.74  892 498 6.2 — Example 13 Comparative 4.46 1235 569 7.3 — Example 14 (Note) *: Aspect ratio = average major axial diameter/average minor axial diameter

TABLE 4 High-density acicular hematite particles Kind of low- Heat treatment for Average Average density acicular high densification major axial minor axial hematite Tempera- Time diameter diameter Examples particles ture (° C.) (min) (μm) (μm) Example 22 Example 4 700 60 0.132 0.0210 Example 23 Example 5 730 60 0.138 0.0223 Example 24 Example 6 750 60 0.138 0.0230 Example 25 Example 7 600 15 0.169 0.0301 Example 26 Example 8 610 15 0.173 0.0288 Example 27 Example 9 650 30 0.186 0.0294 Example 28 Example 10 730 90 0.204 0.0315 Example 29 Example 11 750 120  0.137 0.0222 Example 30 Example 12 800 30 0.139 0.0243 Example 31 Example 13 750 30 0.211 0.0299 Example 32 Example 14 750 60 0.208 0.0296 Example 33 Example 15 730 60 0.189 0.0285 Example 34 Example 16 710 45 0.189 0.0298 Example 35 Example 17 750 30 0.139 0.0220 Example 36 Example 18 780 60 0.140 0.0219 Example 37 Example 19 680 60 0.141 0.0213 Example 38 Example 20 700 30 0.140 0.0211 Example 39 Example 21 700 60 0.142 0.0210 High-density acicular hematite particles Geometrical standard Aspect S_(BET) S_(TEM) S_(BET)/S_(TEM) Examples deviation σg (−) ratio* (−) (m²/g) (m²/g) (−) Example 22 1.35 6.29 51.3 39.5 1.30 Example 23 1.38 6.19 46.8 37.3 1.26 Example 24 1.38 6.00 44.9 36.2 1.24 Example 25 1.35 5.61 38.5 27.8 1.38 Example 26 1.35 6.01 35.1 28.9 1.21 Example 27 1.35 6.33 33.7 28.2 1.19 Example 28 1.34 6.48 34.9 26.3 1.33 Example 29 1.39 6.17 51.0 37.5 1.36 Example 30 1.41 5.72 53.2 34.4 1.55 Example 31 1.44 7.06 37.5 27.5 1.36 Example 32 1.45 7.03 38.9 27.8 1.40 Example 33 1.33 6.63 40.1 29.0 1.38 Example 34 1.34 6.34 37.5 27.8 1.35 Example 35 1.36 6.32 55.9 37.7 1.48 Example 36 1.35 6.39 57.1 37.9 1.51 Example 37 1.36 6.62 51.2 38.8 1.32 Example 38 1.36 6.64 50.6 39.2 1.29 Example 39 1.36 6.76 51.6 39.3 1.31 High-density acicular hematite particles Kind of Sintering preventive Calculated Amount Calculated Amount Calculated Amount Examples as (wt. %) as (wt. %) as (wt. %) Example 22 Sn 14.33 — — — — Example 23 Sn 18.06 — — — — Example 24 Sn 36.83 — — SiO₂ 0.62 Example 25 Sn  1.30 — — — — Example 26 Sn  3.16 — — — — Example 27 Sn 10.06 — — — — Example 28 Sn 35.81 — — — — Example 29 Sn 73.31 — — — — Example 30 Sn 91.68 — — — — Example 31 Sn 55.68 — — — — Example 32 Sn 47.15 P 0.48 — — Example 33 Sn 37.13 Sb 5.14 — — Example 34 Sn  9.65 Sb 2.01 — — Example 35 Sn 49.30 Sb 8.88 SiO₂ 1.41 Example 36 Sn 80.61 Sb 14.31  Al 0.96 Example 37 — — P 1.36 — — Example 38 — — — — SiO₂ 1.83 Example 39 — — P 0.51 SiO₂ 0.70 High-density acicular hematite particles Soluble sodium salt Soluble sulfate pH value Examples (ppm) (ppm) (−) Example 22 1894 3400 5.1 Example 23 2561 3604 4.6 Example 24 2569 3448 5.7 Example 25 1205 3698 5.6 Example 26 1640 3948 5.2 Example 27 3063 3702 4.7 Example 28 3764 3591 5.8 Example 29 4182 3077 6.5 Example 30 5477 3475 6.8 Example 31 2911 4044 4.1 Example 32 2581 3931 4.5 Example 33 2219 2664 5.0 Example 34 2743 4669 4.1 Example 35 3485 2356 7.8 Example 36 3023 2768 6.8 Example 37 2682 3162 5.5 Example 38 2766 3082 5.8 Example 39 2826 3365 5.5 (Note) *: Aspect ratio = average major axial diameter/average minor axial diameter

TABLE 5 Kind of low- High-density acicular density acicular Heat treatment for hematite particles hematite high densification Average Average particles or Tempera- major axial minor axial Comparative acicular goethite ture Time diameter diameter Examples particles (° C.) (min) (μm) (μm) Comparative Example 1 720 15 0.075 0.0336 Example 15 Comparative Comparative 680 15 0.098 0.0286 Example 16 Example 2 Comparative Comparative 700 30 0.125 0.0248 Example 17 Example 4 Comparative Comparative 750 60 0.131 0.0220 Example 18 Example 5 Comparative Comparative 570 90 0.134 0.0206 Example 19 Example 6 Comparative Comparative 720 45 0.134 0.0201 Example 20 Example 7 Comparative Comparative 730 30 0.132 0.0218 Example 21 Example 8 Comparative Comparative 520 90 0.132 0.0198 Example 22 Example 9 Comparative Comparative 720 15 0.191 0.0294 Example 23 Example 10 Comparative Comparative 650 40 0.192 0.0288 Example 24 Example 11 Comparative Comparative 600 15 0.192 0.0290 Example 25 Example 12 Comparative Comparative 750 20 0.190 0.0300 Example 26 Example 13 Comparative Comparative 460 60 0.185 0.0292 Example 27 Example 14 High-density acicular hematite particles Geometrical Aspect Comparative standard ratio* S_(BET) S_(TEM) S_(BET)/S_(TEM) Examples deviation σg (−) (−) (m²/g) (m²/g) (−) Comparative 1.84 2.23 15.8 28.0 0.56 Example 15 Comparative 1.71 3.43 21.9 30.8 0.71 Example 16 Comparative 1.56 5.04 31.8 34.1 0.93 Example 17 Comparative 1.36 5.95 45.6 37.9 1.20 Example 18 Comparative 1.35 6.50 59.3 40.2 1.47 Example 19 Comparative 1.35 6.67 52.6 41.1 1.28 Example 20 Comparative 1.36 6.06 43.6 38.2 1.14 Example 21 Comparative 1.34 6.67 68.9 41.8 1.65 Example 22 Comparative 1.34 6.50 35.2 28.2 1.25 Example 23 Comparative 1.33 6.67 43.9 28.7 1.53 Example 24 Comparative 1.33 6.62 51.5 28.5 1.81 Example 25 Comparative 1.34 6.33 37.5 27.7 1.36 Example 26 Comparative 1.33 6.34 65.0 28.4 2.29 Example 27 High-density acicular hematite particles Kind of Sintering preventive Soluble Soluble Volume Comparative Calculated Amount sodium sulfate pH value resistivity Example as (wt. %) salt (ppm) (ppm) (−) (Ωcm) Comparative — — 1658 3256 5.3 5.6 × 10⁸ Example 15 Comparative — — 1745 3569 5.3 8.9 × 10⁸ Example 16 Comparative P 0.44 1652 3756 5.1 3.8 × 10⁸ Example 17 Comparative SiO₂ 0.93 1548 3874 4.9 7.1 × 10⁸ Example 18 Comparative P 0.46 1436 2964 5.3 — Example 19 Comparative SiO₂ 1.40 1569 3684 5.1 — Example 20 Comparative SiO₂ 0.21 1856 3548 5.2 — Example 21 Comparative P 0.74 1329 2456 5.6 — Example 22 Comparative P 1.83 1954 3659 5.0 3.8 × 10⁸ Example 23 Comparative SiO₂ 1.22 2045 3246 5.6 — Example 24 Comparative P 1.46 1564 2857 5.2 — Example 25 Comparative SiO₂ 0.23 1186 3156 4.7 — Example 26 Comparative Sn 0.05 2356 3247 5.6 — Example 27 (Note) *: Aspect ratio = average major axial diameter/average minor axial diameter

TABLE 6 Kind of high- Wet-pulverization Heat treatment density step in aqueous acicular Residue alkaline solution hematite Use or on sieve pH Tempera- Time Examples particles non-use (wt. %) (−) ture (° C.) (min) Example 40 Example 22 used 0 13.1 98 180 Example 41 Example 23 used 0 13.5 94 180 Example 42 Example 24 used 0 13.3 95 180 Example 43 Example 25 used 0 13.8 91 120 Example 44 Example 26 used 0 13.8 95 90 Example 45 Example 27 used 0 13.5 95 90 Example 46 Example 28 used 0 13.6 95 180 Example 47 Example 29 used 0 13.5 92 180 Example 48 Example 30 used 0 13.7 95 120 Example 49 Example 31 used 0 13.3 90 120 Example 50 Example 32 used 0 13.5 97 120 Example 51 Example 33 used 0 13.8 97 60 Example 52 Example 34 used 0 13.7 95 60 Example 53 Example 35 used 0 13.2 90 120 Example 54 Example 36 used 0 13.6 95 180 Example 55 Example 37 used 0 13.1 95 180 Example 56 Example 38 used 0 13.5 95 180 Example 57 Example 39 used 0 13.3 95 180

TABLE 7 Acicular hematite particles washed with water after aqueous alkaline solution treatment Average major Average minor Geometrical axial diameter axial diameter standard Aspect ratio* Examples (μm) (μm) deviation σg (−) (−) Example 40 0.132 0.0209 1.35 6.32 Example 41 0.138 0.0223 1.38 6.19 Example 42 0.137 0.0230 1.38 5.96 Example 43 0.170 0.0301 1.35 5.65 Example 44 0.172 0.0288 1.34 5.97 Example 45 0.186 0.0294 1.35 6.33 Example 46 0.203 0.0314 1.34 6.46 Example 47 0.138 0.0222 1.39 6.22 Example 48 0.139 0.0243 1.40 5.72 Example 49 0.210 0.0298 1.44 7.05 Example 50 0.209 0.0296 1.44 7.06 Example 51 0.188 0.0285 1.34 6.60 Example 52 0.189 0.0298 1.35 6.34 Example 53 0.140 0.0220 1.36 6.36 Example 54 0.140 0.0219 1.37 6.39 Example 55 0.141 0.0213 1.36 6.62 Example 56 0.141 0.0211 1.36 6.68 Example 57 0.143 0.0210 1.36 6.81 Acicular hematite particles washed with water after aqueous alkaline solution treatment S_(BET) S_(TEM) S_(BET)/S_(TEM) Examples (m²/g) (m²/g) (−) Example 40 52.2 39.7 1.31 Example 41 47.1 37.3 1.26 Example 42 43.7 36.3 1.21 Example 43 38.9 27.8 1.40 Example 44 36.1 28.9 1.25 Example 45 34.0 28.2 1.20 Example 46 35.5 26.4 1.35 Example 47 50.6 37.4 1.35 Example 48 52.5 34.4 1.53 Example 49 36.9 27.6 1.33 Example 50 38.3 27.8 1.38 Example 51 40.8 29.0 1.41 Example 52 36.8 27.8 1.32 Example 53 54.8 37.7 1.45 Example 54 56.5 37.9 1.49 Example 55 50.6 38.8 1.30 Example 56 50.8 39.2 1.30 Example 57 51.9 39.3 1.32 Acicular hematite particles washed with water after aqueous alkaline solution treatment Kind of Sintering preventive Calculated Amount Calculated Amount Calculated Amount Examples as (wt. %) as (wt. %) as (wt. %) Example 40 Sn 14.16 — — — — Example 41 Sn 17.92 — — — — Example 42 Sn 36.65 — — SiO₂ 0.60 Example 43 Sn  1.30 — — — — Example 44 Sn  3.14 — — — — Example 45 Sn  9.68 — — — — Example 46 Sn 35.60 — — — — Example 47 Sn 72.10 — — — — Example 48 Sn 90.01 — — — — Example 49 Sn 53.65 — — — — Example 50 Sn 45.89 P 0.26 — — Example 51 Sn 35.68 Sb 5.16 — — Example 52 Sn  9.26 Sb 1.86 — — Example 53 Sn 48.65 Sb 8.62 SiO₂ 1.36 Example 54 Sn 76.56 Sb 13.68  Al 0.98 Example 55 — — P 0.72 — — Example 56 — — — — SiO₂ 1.80 Example 57 — — p 0.25 SiO₂ 0.68 Acicular hematite particles washed with water after aqueous alkaline solution treatment Soluble sodium Volume salt Soluble sulfate pH value resistivity Examples (ppm) (ppm) (−) (Ωcm) Example 40 108 13 9.3 3.2 × 10⁶ Example 41 135 32 9.0 1.7 × 10⁶ Example 42  87 23 9.1 1.1 × 10⁶ Example 43  78 24 8.8 3.8 × 10⁷ Example 44 121 32 9.4 3.1 × 10⁷ Example 45  98 46 8.6 8.2 × 10⁶ Example 46 105 48 8.9 1.0 × 10⁶ Example 47 124 11 9.0 5.8 × 10⁵ Example 48 138 21 9.5 2.6 × 10⁵ Example 49  76 15 8.8 9.1 × 10⁵ Example 50  89 21 8.9 7.0 × 10⁵ Example 51 107 17 9.3 6.9 × 10⁵ Example 52 124 16 9.1 2.6 × 10⁶ Example 53  79  8 9.0 3.3 × 10⁵ Example 54  87  8 8.9 1.3 × 10⁵ Example 55 115 15 9.2 8.9 × 10⁸ Example 56 121 21 9.4 6.5 × 10⁸ Example 57  89 32 8.9 5.1 × 10⁸ (Note) *: Aspect ratio = average major axial diameter/average minor axial diameter

TABLE 8 Wet-pulverization Heat treatment Kind of step in aqueous acicular Residue alkaline solution Comparative hematite Use or on sieve pH Tempera- Time Examples particles non-use (wt. %) (−) ture (° C.) (min) Comparative Comparative used 0 — — — Example 28 Example 19 Comparative Comparative used 0 11.5 93 180 Example 29 Example 20 Comparative Comparative used 0 13.3 50 180 Example 30 Example 21 Comparative Comparative unused 18.0 13.3 90 180 Example 31 Example 22 Comparative Comparative unused 19.6 10.5 95 180 Example 32 Example 24 Comparative Comparative unused 23.6 13.3 92 120 Example 33 Example 25 Comparative Comparative unused 17.5 13.5 90 120 Example 34 Example 26 Comparative Comparative used 0  9.5 95 120 Example 35 Example 27

TABLE 9 Acicular hematite particles washed with water after aqueous alkaline solution treatment Average major Average minor Geometrical Comparative axial diameter axial diameter standard Aspect ratio* Examples (μm) (μ m) deviation σg (−) (−) Comparative 0.134 0.0206 1.35 6.50 Example 28 Comparative 0.134 0.0200 1.35 6.70 Example 29 Comparative 0.132 0.0218 1.35 6.06 Example 30 Comparative 0.132 0.0198 1.35 6.67 Example 31 Comparative 0.192 0.0288 1.35 6.67 Example 32 Comparative 0.192 0.0291 1.34 6.60 Example 33 Comparative 0.191 0.0302 1.35 6.32 Example 34 Comparative 0.185 0.0292 1.33 6.34 Example 35 Acicular hematite particles washed with water after aqueous alkaline solution treatment Comparative S_(BET) S_(TEM) S_(BET)/S_(TEM) Examples (m²/g) (m²/g) (−) Comparative 58.8 40.2 1.46 Example 28 Comparative 52.6 41.3 1.27 Example 29 Comparative 44.1 38.2 1.15 Example 30 Comparative 69.1 41.8 1.65 Example 31 Comparative 43.7 28.7 1.52 Example 32 Comparative 50.9 28.4 1.79 Example 33 Comparative 38.0 27.5 1.38 Example 34 Comparative 63.8 28.4 2.24 Example 35 Acicular hematite particles washed with water after aqueous alkaline solution treatment Kind of Sintering Specific preventive Soluble Soluble volume Comparative Calculated Amount sodium sulfate pH value resistivity Examples as (wt. %) salt (ppm) (ppm) (−) (Ωcm) Comparative P 0.46 658 354 7.1 5.1 × 10⁸ Example 28 Comparative SiO₂ 1.38 452 316 7.0 6.7 × 10⁸ Example 29 Comparative SiO₂ 0.21 365 197 7.7 7.4 × 10⁸ Example 30 Comparative P 0.75 312 165 7.9 8.0 × 10⁸ Example 31 Comparative SiO₂ 1.20 703 335 7.0 6.1 × 10⁸ Example 32 Comparative P 1.44 321 185 7.5 7.9 × 10⁸ Example 33 Comparative SiO₂ 0.23 376 167 7.9 3.7 × 10⁸ Example 34 Comparative SiO₂ 0.04 832 349 7.1 8.6 × 10⁷ Example 35 (Note) *: Aspect ratio = average major axial diameter/average minor axial diameter

TABLE 10 Kind of acicular Surface treatment hematite Amount particles added treated with (calculated aqueous as each Coating substance alkaline element) Calculated Amount Examples solution Kind (wt. %) as (wt. %) Example 58 Example 40 Sodium 1.3 Al 1.28 aluminate Example 59 Example 41 Water 0.5 SiO₂ 0.45 glass #3 Example 60 Example 42 Aluminum 1.0 Al 0.99 sulfate Example 61 Example 43 Colloidal 1.0 SiO₂ 0.96 silica Example 62 Example 44 Aluminum 1.5 Al 1.46 acetate Water 0.8 SiO₂ 0.77 glass #3 Example 63 Example 45 Aluminum 0.3 Al 0.30 sulfate Water 2.5 SiO₂ 2.38 glass #3 Example 64 Example 46 Sodium 5.0 Al 4.76 aluminate Example 65 Example 47 Sodium 1.5 Al 1.46 aluminate Colloidal 2.5 SiO₂ 2.36 silica Example 66 Example 48 Sodium 0.2 Al 0.20 aluminate Example 67 Example 49 Aluminum 10.0 Al 9.01 acetate Colloidal 0.3 SiO₂ 0.28 silica Example 68 Example 50 Water 3.0 SiO₂ 2.90 glass #3 Example 69 Example 51 Sodium 1.8 Al 1.76 aluminate Example 70 Example 52 Aluminum 0.2 Al 0.20 acetate Example 71 Example 53 Sodium 3.0 Al 2.91 aluminate Example 72 Example 54 Water 1.5 SiO₂ 1.45 glass #3 Example 73 Example 55 Sodium 3.0 Sn 2.90 stannate Example 74 Example 56 Stannous 5.0 Sn 4.71 chloride Example 75 Example 57 Sodium 5.5 Sn 5.11 stannate Antimony 0.5 Sb 0.47 chloride

TABLE 11 Properties of acicular hematite particles washed with water after aqueous alkaline solution treatment Average major Average minor Geometrical axial diameter axial diameter standard Aspect ratio* Examples (μm) (μm) deviation σg (−) (−) Example 58 0.132 0.0209 1.35 6.32 Example 59 0.137 0.0222 1.38 6.17 Example 60 0.137 0.0231 1.38 5.93 Example 61 0.170 0.0300 1.35 5.67 Example 62 0.171 0.0288 1.35 5.94 Example 63 0.187 0.0294 1.35 6.36 Example 64 0.202 0.0313 1.34 6.45 Example 65 0.138 0.0222 1.39 6.22 Example 66 0.139 0.0244 1.40 5.70 Example 67 0.209 0.0298 1.44 7.01 Example 68 0.210 0.0296 1.44 7.09 Example 69 0.188 0.0285 1.34 6.60 Example 70 0.189 0.0298 1.35 6.34 Example 71 0.141 0.0221 1.36 6.38 Example 72 0.140 0.0220 1.37 6.36 Example 73 0.141 0.0213 1.36 6.62 Example 74 0.141 0.0211 1.36 6.68 Example 75 0.143 0.0210 1.36 6.81 Properties of acicular hematite particles washed with water after aqueous alkaline solution treatment S_(BET) S_(TEM) S_(BET)/S_(TEM) Examples (m²/g) (m²/g) (−) Example 58 51.9 39.7 1.31 Example 59 46.9 37.5 1.25 Example 60 43.2 36.1 1.20 Example 61 38.7 27.9 1.39 Example 62 36.0 29.0 1.24 Example 63 35.3 28.2 1.25 Example 64 36.5 26.5 1.38 Example 65 52.3 37.4 1.40 Example 66 51.5 34.3 1.50 Example 67 40.0 27.7 1.45 Example 68 40.8 27.8 1.47 Example 69 40.1 29.0 1.38 Example 70 36.5 27.8 1.31 Example 71 55.1 37.5 1.47 Example 72 55.6 37.7 1.47 Example 73 51.0 38.8 1.31 Example 74 52.6 39.2 1.34 Example 75 52.6 39.3 1.34 Properties of acicular hematite particles washed with water after aqueous alkaline solution treatment Kind of Sintering preventive Calculated Amount Calculated Amount Calculated Amount Examples as (wt. %) as (wt. %) as (wt. %) Example 58 Sn 13.75 — — — — Example 59 Sn 17.68 — — — — Example 60 Sn 34.52 — — SiO₂ 0.58 Example 61 Sn  1.28 — — — — Example 62 Sn  3.06 — — — — Example 63 Sn  9.22 — — — — Example 64 Sn 33.81 — — — — Example 65 Sn 70.12 — — — — Example 66 Sn 88.82 — — — — Example 67 Sn 48.77 — — — — Example 68 Sn 44.00 P 0.25 — — Example 69 Sn 34.68 Sb 5.11 — — Example 70 Sn  8.92 Sb 1.83 — — Example 71 Sn 47.32 Sb 8.58 SiO₂ 1.36 Example 72 Sn 74.82 Sb 12.99  Al 0.98 Example 73 — — P 0.69 — — Example 74 — — — — SiO₂ 1.71 Example 75 — — P 0.23 SiO₂ 0.64 Properties of acicular hematite particles washed with water after aqueous alkaline solution treatment Soluble sodium Volume salt Soluble sulfate pH value resistivity Examples (ppm) (ppm) (−) (Ωcm) Example 58 97  9 9.3 4.1 × 10⁶ Example 59 76 13 9.0 1.8 × 10⁶ Example 60 65  6 9.4 1.3 × 10⁶ Example 61 85 12 8.9 5.0 × 10⁷ Example 62 56  2 9.6 4.5 × 10⁷ Example 63 123  12 9.3 1.2 × 10⁷ Example 64 76 10 9.0 2.3 × 10⁶ Example 65 107   7 9.2 6.9 × 10⁵ Example 66 65  5 9.6 2.5 × 10⁵ Example 67 135  34 8.8 2.4 × 10⁶ Example 68 87 12 9.1 9.3 × 10⁵ Example 69 54 11 9.0 8.8 × 10⁵ Example 70 46  2 9.2 2.7 × 10⁶ Example 71 68 16 9.0 6.4 × 10⁵ Example 72 100  11 8.9 2.5 × 10⁵ Example 73 89 12 9.2 6.8 × 10⁸ Example 74 78  6 9.3 3.2 × 10⁸ Example 75 66 11 9.0 1.1 × 10⁸ (Note) *: Aspect ratio = average major axial diameter/average minor axial diameter

TABLE 12 Kind of high- density Heat treatment acicular Tempera- Coating substance hematite ture Time Calculated Amount Examples particles (° C.) (min) as (wt. %) Example 76 Example 73 400 60 Sn 2.92 Example 77 Example 74 350 60 Sn 4.75 Example 78 Example 75 380 90 Sn 5.32 Sb 0.49

TABLE 13 Properties of acicular hematite particles washed with water after treatment with tin compound Geometrical Average major Average minor standard Aspect axial diameter axial diameter deviation ratio* Examples (μm) (μm) σg (−) (—) Example 76 0.141 0.0213 1.36 6.62 Example 77 0.141 0.0210 1.36 6.71 Example 78 0.143 0.0209 1.36 6.84 S_(BET) S_(TEM) S_(BET)/S_(TEM) Examples (m²/g) (m²/g) (−) Example 76 50.6 38.8 1.30 Example 77 51.1 39.4 1.30 Example 78 51.9 39.5 1.31 Kind of Sintering preventive Examples Calculated as Amount (wt. %) Example 76 P 0.70 Example 77 SiO₂ 1.74 Example 78 P 0.24 SiO₂ 0.67 Soluble sodium Volume salt Soluble sulfate pH value resistivity Examples (ppm) (ppm) (−) (Ωcm) Example 76 125 15 8.9 2.6 × 10⁶ Example 77 115 26 9.0 8.1 × 10⁶ Example 78  91 32 9.0 1.6 × 10⁶ (Note)*:Aspect ratio = average major axial diameter/average minor axial diameter

TABLE 14 Production of non-magnetic coating material Non-magnetic Kind of coating acicular Weight ratio material hematite of particles Viscosity Examples particles to resin (−) (cP) Example 79 Example 40 5.0 410 Example 80 Example 41 5.0 435 Example 81 Example 42 5.0 384 Example 82 Example 43 5.0 333 Example 83 Example 44 5.0 205 Example 84 Example 45 5.0 179 Example 85 Example 46 5.0 128 Example 86 Example 47 5.0 742 Example 87 Example 48 5.0 896 Example 88 Example 49 5.0 205 Example 89 Example 50 5.0 230 Example 90 Example 51 5.0 512 Example 91 Example 52 5.0 384 Example 92 Example 53 5.0 768 Example 93 Example 54 5.0 819 Example 94 Example 58 5.0 384 Example 95 Example 59 5.0 384 Non-magnetic undercoat layer Young's Thickness Surface modulus of coating Gloss roughness (relative Examples layer (μm) (%) Ra (nm) value) Example 79 3.5 190 7.2 126 Example 80 3.4 186 7.5 124 Example 81 3.4 181 7.8 125 Example 82 3.4 198 6.8 129 Example 83 3.3 196 6.8 127 Example 84 3.5 194 7.6 133 Example 85 3.5 188 8.4 131 Example 86 3.4 185 8.8 124 Example 87 3.3 180 10.4  123 Example 88 3.5 187 3.0 134 Example 89 3.4 191 7.8 136 Example 90 3.5 195 7.4 128 Example 91 3.4 199 7.0 131 Example 92 3.5 185 8.6 124 Example 93 3.5 185 8.3 126 Example 94 3.4 185 7.0 128 Example 95 3.5 180 7.3 125

TABLE 15 Production of non-magnetic coating material Non-magnetic Kind of Weight ratio coating acicular of particles material hematite to resin Viscosity Examples particles (−) (cP) Example 96 Example 60 5.0 307 Example 97 Example 61 5.0 333 Example 98 Example 62 5.0 179 Example 99 Example 63 5.0 123 Example 100 Example 64 5.0 102 Example 101 Example 65 5.0 512 Example 102 Example 66 5.0 768 Example 103 Example 67 5.0 179 Example 104 Example 68 5.0 205 Example 105 Example 69 5.0 384 Example 106 Example 70 5.0 230 Example 107 Example 71 5.0 410 Example 108 Example 72 5.0 435 Example 109 Example 76 5.0 384 Example 110 Example 77 5.0 435 Example 111 Example 78 5.0 512 Non-magnetic undercoat layer Young's Thickness Surface modulus of coating Gloss roughness (relative Examples layer (μm) (%) Ra (nm) value) Example 96 3.4 191 7.3 127 Example 97 3.4 205 6.8 131 Example 98 3.4 200 6.5 131 Example 99 3.3 193 7.4 136 Example 100 3.4 195 7.9 134 Example 101 3.4 190 8.3 125 Example 102 3.5 188 8.6 125 Example 103 3.5 193 8.8 136 Example 104 3.4 194 8.5 139 Example 105 3.5 196 8.0 131 Example 106 3.4 207 6.8 135 Example 107 3.3 190 7.4 127 Example 108 3.4 195 7.3 127 Example 109 3.4 195 7.5 128 Example 110 3.4 198 7.2 128 Example 111 3.4 201 6.9 129

TABLE 16 Production of non-magnetic coating material Non-magnetic Kind of Weight ratio coating acicular of particles material Comparative hematite to resin Viscosity Examples particles (−) (cP) Comparative Comparative 5.0 25600 Example 36 Example 1 Comparative Comparative 5.0 128 Example 37 Example 15 Comparative Comparative 5.0 102 Example 38 Example 16 Comparative Comparative 5.0 20480 Example 39 Example 3 Comparative Comparative 5.0 768 Example 40 Example 17 Comparative Comparative 5.0 563 Example 41 Example 18 Comparative Comparative 5.0 435 Example 42 Example 28 Comparative Comparative 5.0 405 Example 43 Example 29 Comparative Comparative 5.0 384 Example 44 Example 30 Comparative Comparative 5.0 640 Example 45 Example 31 Comparative Comparative 5.0 512 Example 46 Example 23 Comparative Comparative 5.0 435 Example 47 Example 32 Comparative Comparative 5.0 435 Example 48 Example 33 Comparative Comparative 5.0 410 Example 49 Example 34 Comparative Comparative 5.0 2560 Example 50 Example 35 Non-magnetic undercoat layer Young's Thickness Surface modulus Comparative of coating Gloss roughness (relative Examples layer (μm) (%) Ra (nm) value) Comparative 3.6 68 112.0 76 Example 36 Comparative 3.5 45 181.0 58 Example 37 Comparative 3.5 89 78.5 86 Example 38 Comparative 3.7 76 84.0 77 Example 39 Comparative 3.5 135 33.8 103 Example 40 Comparative 3.5 159 23.1 105 Example 41 Comparative 3.5 170 15.9 110 Example 42 Comparative 3.6 176 13.1 112 Example 43 Comparative 3.5 175 13.2 110 Example 44 Comparative 3.6 165 17.0 105 Example 45 Comparative 3.7 147 21.7 109 Example 46 Comparative 3.6 167 18.6 112 Example 47 Comparative 3.8 171 16.2 110 Example 48 Comparative 3.5 175 14.4 114 Example 49 Comparative 3.6 148 22.7 104 Example 50

TABLE 17 Magnetic recording medium using magnetic particles containing iron as main ingredient Weight ratio Kind of mag- Non- netic magnetic particles undercoat Kind of magnetic particles to resin Examples layer containing iron as main ingredient (−) Example 112 Example 79 [major axial diameter = 0.10 μm; 5.0 minor axial diameter = 0.016 μm; Example 113 Example 80 aspect ratio = 6.3; 5.0 Example 114 Example 81 Hc = 1926 Oe; 5.0 Example 115 Example 82 σs = 131.0 emu/g; 5.0 Example 116 Example 83 pH value = 10.3; 5.0 Example 117 Example 84 Al content = 4.11 wt. %; 5.0 Example 118 Example 85 Co content = 5.87 wt. %] 5.0 Example 119 Example 86 [major axial diameter = 0.12 μm; 5.0 Example 120 Example 87 minor axial diameter = 0.018 μm; 5.0 Example 121 Example 88 aspect ratio = 7.0; 5.0 Example 122 Example 89 Hc = 1770 Oe; 5.0 Example 123 Example 90 σs = 138.0 emu/g; 5.0 Example 124 Example 91 pH value = 9.8; 5.0 Example 125 Example 92 Al content = 2.27 wt. %; 5.0 Example 126 Example 93 Co content = 3.72 wt. %] 5.0 Thickness of Coercive Surface magnetic force Br/Bm Gloss roughness Examples layer (μm) (Oe) (−) (%) Ra (nm) Example 112 1.1 2022 0.88 210 7.0 Example 113 1.1 2035 0.88 206 7.0 Example 114 1.1 2041 0.88 205 7.6 Example 115 1.0 2087 0.88 221 6.4 Example 116 1.1 2036 0.88 223 6.3 Example 117 1.1 2026 0.87 212 7.0 Example 118 1.1 2016 0.88 208 7.4 Example 119 1.1 1856 0.89 203 8.0 Example 120 1.2 1836 0.87 196 8.6 Example 121 1.1 1897 0.88 200 7.6 Example 122 1.0 1893 0.89 211 7.4 Example 123 1.1 1834 0.89 209 7.2 Example 124 1.1 1867 0.90 227 6.5 Example 125 1.2 1870 0.88 213 7.0 Example 126 1.1 1867 0.88 216 7.0 Corrosion property Young's Linear Rate of modulus absorption Surface change in Rate of (relative coefficient resistivity coercive change in Examples value) (μm⁻¹) (Ω/sq) force (%) Bm (%) Example 112 131 1.23 9.6 × 10⁷ 7.9 6.9 Example 113 130 1.24 5.1 × 10⁷ 6.4 5.4 Example 114 132 1.21 9.8 × 10⁷ 5.3 5.8 Example 115 134 1.27 4.6 × 10⁷ 5.7 6.9 Example 116 134 1.29 4.4 × 10⁷ 7.3 6.4 Example 117 138 1.31 1.8 × 10⁸ 3.7 4.8 Example 118 135 1.31 8.8 × 10⁷ 6.4 7.9 Example 119 130 1.20 6.4 × 10⁶ 4.8 6.3 Example 120 131 1.20 7.8 × 10⁵ 5.3 7.2 Example 121 139 1.30 8.6 × 10⁶ 8.6 7.6 Example 122 141 1.31 7.3 × 10⁶ 7.4 7.9 Example 123 132 1.28 1.0 × 10⁷ 5.8 6.8 Example 124 133 1.26 7.8 × 10⁷ 6.7 5.2 Example 125 130 1.23 6.5 × 10⁶ 6.6 4.8 Example 126 130 1.22 8.7 × 10⁵ 3.6 3.5

TABLE 18 Magnetic recording medium using magnetic particles containing iron as main ingredient Weight ratio Kind of mag- Non- netic magnetic particles undercoat Kind of magnetic particles to resin Examples layer containing iron as main ingredient (−) Example 127 Example 94 [major axial diameter = 0.10 μm; 5.0 minor axial diameter = 0.016 μm; Example 128 Example 95 aspect ratio = 6.3; 5.0 Example 129 Example 96 Hc = 1926 Oe; 5.0 Example 130 Example 97 σs = 131.0 emu/g; 5.0 Example 131 Example 98 pH value = 10.3; 5.0 Example 132 Example 99 Al content = 4.11 wt. %; 5.0 Example 133 Example 100 Co content = 5.87 wt. %] 5.0 Example 134 Example 101 [major axial diameter = 0.12 μm; 5.0 Example 135 Example 102 minor axial diameter = 0.018 μm; 5.0 Example 136 Example 103 aspect ratio = 7.0; 5.0 Example 137 Example 104 Hc = 1770 Oe; 5.0 Example 138 Example 105 σs = 138.0 emu/g; 5.0 Example 139 Example 106 pH value = 9.8; 5.0 Example 140 Example 107 Al content = 2.27 wt. %; 5.0 Example 141 Example 108 Co content = 3.72 wt. %] 5.0 Example 142 Example 109 5.0 Example 143 Example 110 5.0 Example 144 Example 111 5.0 Thickness of Coercive Surface magnetic force Br/Bm Gloss roughness Examples layer (μm) (Oe) (−) (%) Ra (nm) Example 127 1.1 2032 0.89 223 6.8 Example 128 1.1 2043 0.88 215 7.0 Example 129 1.1 2036 0.89 209 7.3 Example 130 1.0 2075 0.88 220 6.4 Example 131 1.1 2046 0.90 225 6.2 Example 132 1.1 2050 0.89 227 6.8 Example 133 1.2 2043 0.90 219 7.2 Example 134 1.2 1864 0.90 218 7.6 Example 135 1.2 1845 0.88 209 9.0 Example 136 1.1 1887 0.88 210 7.4 Example 137 1.1 1895 0.90 217 7.0 Example 138 1.0 1845 0.90 217 7.0 Example 139 1.1 1876 0.91 236 6.1 Example 140 1.1 1881 0.88 218 6.8 Example 141 1.1 1875 0.89 223 6.7 Example 142 1.2 1881 0.89 211 7.5 Example 143 1.1 1872 0.90 215 7.3 Example 144 1.1 1865 0.90 216 7.0 Corrosion property Young's Linear Rate of modulus absorption Surface change in Rate of (relative coefficient resistivity coercive change in Examples value) (μm⁻¹) (Ω/sq) force (%) Bm (%) Example 127 134 1.24 9.6 × 10⁷ 4.5 4.7 Example 128 130 1.24 5.3 × 10⁷ 5.4 4.9 Example 129 133 1.23 1.0 × 10⁸ 4.5 4.7 Example 130 136 1.27 4.6 × 10⁸ 5.5 6.6 Example 131 137 1.29 4.8 × 10⁸ 6.8 6.3 Example 132 141 1.32 2.5 × 10⁸ 3.2 3.8 Example 133 138 1.31 9.9 × 10⁷ 3.6 4.7 Example 134 130 1.21 7.2 × 10⁶ 3.7 5.1 Example 135 131 1.21 8.5 × 10⁵ 5.0 6.4 Example 136 139 1.30 9.0 × 10⁶ 6.8 6.5 Example 137 144 1.30 8.7 × 10⁶ 6.1 6.0 Example 138 132 1.28 2.1 × 10⁷ 4.7 5.5 Example 139 140 1.27 8.4 × 10⁷ 5.4 4.1 Example 140 134 1.23 8.0 × 10⁶ 2.9 3.7 Example 141 135 1.23 9.8 × 10⁵ 2.8 2.9 Example 142 133 1.23 3.6 × 10⁸ 7.2 6.8 Example 143 134 1.23 2.1 × 10⁸ 8.1 6.8 Example 144 135 1.24 9.6 × 10⁷ 6.0 5.2

TABLE 19 Magnetic recording medium using magnetic particles containing iron as main ingredient Weight ratio Kind of mag- Non- netic magnetic particles Comparative undercoat Kind of magnetic particles to resin Examples layer containing iron as main ingredient (−) Comparative Comparative [major axial diameter = 0.10 μm; 5.0 Example 51 Example 36 minor axial diameter = 0.016 μm; Comparative Comparative aspect ratio = 6.3; 5.0 Example 52 Example 37 Hc = 1926 Oe; Comparative Comparative σs = 131.0 emu/g; 5.0 Example 53 Example 38 pH value = 10.3; Comparative Comparative Al content = 4.11 wt. %; 5.0 Example 54 Example 39 Co content = 5.87 wt. %] Comparative Comparative 5.0 Example 55 Example 40 Comparative Comparative 5.0 Example 56 Example 41 Comparative Comparative 5.0 Example 57 Example 42 Comparative Comparative 5.0 Example 58 Example 43 Comparative Comparative 5.0 Example 59 Example 44 Comparative Comparative 5.0 Example 60 Example 45 Comparative Comparative 5.0 Example 61 Example 46 Comparative Comparative 5.0 Example 62 Example 47 Comparative Comparative 5.0 Example 63 Example 48 Comparative Comparative 5.0 Example 64 Example 49 Comparative Comparative 5.0 Example 65 Example 50 Thickness of Coercive Surface Comparative magnetic force Br/Bm Gloss roughness Examples layer (μm) (Oe) (−) (%) Ra (nm) Comparative 1.3 1976 0.77 123 76.5 Example 51 Comparative 1.2 1987 0.81 132 68.3 Example 52 Comparative 1.2 1980 0.82 165 31.6 Example 53 Comparative 1.2 1991 0.78 154 46.2 Example 54 Comparative 1.2 2001 0.83 175 17.9 Example 55 Comparative 1.3 2010 0.84 187 13.2 Example 56 Comparative 1.1 2018 0.86 191 11.8 Example 57 Comparative 1.3 2028 0.87 194 11.6 Example 58 Comparative 1.1 1999 0.86 190 12.6 Example 59 Comparative 1.2 2007 0.84 177 14.7 Example 60 Comparative 1.1 1989 0.84 165 21.6 Example 61 Comparative 1.0 2011 0.85 181 13.8 Example 62 Comparative 1.3 1997 0.85 188 12.1 Example 63 Comparative 1.3 2023 0.85 188 11.9 Example 64 Comparative 1.2 2017 0.84 165 23.8 Example 65 Corrosion property Young's Linear Rate of modulus absorption Surface change in Rate of Comparative (relative coefficient resistivity coercive change in Examples value) (μm⁻¹) (Ω/sq) force (%) Bm (%) Comparative 90 0.84 8.9 × 10⁸ 27.5 25.4 Example 51 Comparative 73 0.90 8.3 × 10⁸ 38.9 31.1 Example 52 Comparative 96 0.95 9.6 × 10⁸ 49.8 36.8 Example 53 Comparative 89 0.99 1.1 × 10⁹ 28.2 23.7 Example 54 Comparative 113 1.09 1.3 × 10⁹ 46.9 39.7 Example 55 Comparative 116 1.13 8.7 × 10⁸ 37.6 33.3 Example 56 Comparative 121 1.15 2.3 × 10⁹ 17.1 15.8 Example 57 Comparative 116 1.15 1.0 × 10¹⁰ 14.2 13.8 Example 58 Comparative 121 1.14 7.2 × 10⁹ 16.4 16.7 Example 59 Comparative 121 1.17 3.6 × 10⁹ 16.3 19.0 Example 60 Comparative 116 1.19 1.8 × 10⁹ 37.4 31.6 Example 61 Comparative 121 1.19 4.1 × 10⁹ 18.9 23.1 Example 62 Comparative 119 1.17 7.2 × 10⁹ 15.7 18.5 Example 63 Comparative 123 1.18 6.5 × 10⁹ 18.5 16.9 Example 64 Comparative 118 1.06 9.6 × 10⁸ 23.7 24.8 Example 65 

What is claimed is:
 1. An undercoat layer on a non-magnetic substrate, comprising a binder resin and high-density acicular hematite particles comprising acicular hematite particles and a coat comprising an oxide of tin or oxides of tin and antimony, formed on at least a part of the surfaces of said acicular hematite particles; and having an average major axial diameter of not more than 0.3 μm, a pH value of not less than 8, a soluble sodium salt content of not more than 300 ppm, calculated as Na, a soluble sulfate content of not more than 150 ppm, calculated as SO₄ and a volume resistivity of 10³ to 5×10⁷ Ωcm.
 2. An undercoat layer according to claim 1, wherein the amount of said high-density acicular hematite particles is 5 to 2,000 parts by weight based on 100 parts by weight of said binder resin.
 3. An undercoat layer according to claim 1, which have a thickness of 0.2 to 10.0 μm.
 4. An undercoat layer according to claim 1, which further have a gloss of 180 to 280% and a surface roughness of 2.0 to 13.0 nm.
 5. An undercoat layer according to claim 1, wherein said acicular hematite particle has a coat comprising at least one compound selected from the group consisting of a hydroxide of aluminum, an oxide of aluminum, a hydroxide of silicon and an oxide of silicon, on a least a part of surface of the acicular hematite particle.
 6. An undercoat layer according to claim 1, wherein said acicular hematite particles are coated with an oxide of tin in an amount of 0.5 to 500% by weight, calculated as Sn, based on the weight of said acicular hematite particles.
 7. An undercoat layer according to claim 1, wherein said acicular hematite particles are coated with an oxide of antimony in an amount of 0.05 to 50% by weight, calculated as Sb, based on the weight of said acicular hematite particles.
 8. An undercoat layer according to claim 1, wherein said acicular hematite particles have a weight ratio of tin to antimony of 20:1 to 1:1.
 9. An undercoat layer according to claim 1, wherein said acicular hematite particles have an aspect ratio (average major axial diameter:average minor axial diameter) of not less than 2:1.
 10. An undercoat layer according to claim 1, wherein said acicular hematite particles have a degree of densification (S_(BET)/S_(TEM)) of 0.5 to 2.5, wherein S_(BET) represents a specific surface area measured by a BET method, and S_(STEM) represents a surface area calculated from values of major axial diameter and minor axial diameter obtained by measurement of particles on electron microscope photograph.
 11. An undercoat layer according to claim 1, wherein said acicular hematite particles have a particle size distribution of major axial diameter represented by a geometrical standard deviation of not more than 1.50.
 12. An undercoat layer according to claim 1, wherein said acicular hematite particles have a BET specific surface area of not less than 35 m²/g. 